Glass containers with improved strength and improved damage tolerance

ABSTRACT

Glass pharmaceutical packages comprising glass containers are disclosed. In embodiments, a coated glass pharmaceutical package includes a glass container formed from one of a borosilicate glass composition that meets Type 1 criteria according to USP &lt;660&gt; or an alkali aluminosilicate glass having a Class HGA 1 hydrolytic resistance when tested according to the ISO 720-1985 testing standard. A lubricous coating may be positioned on at least a portion of the exterior surface of the glass container. The portion of the coated glass pharmaceutical package with the lubricous coating has a coefficient of friction that is at least 20% less than an uncoated glass pharmaceutical package. A horizontal compression strength of the portion of the coated glass pharmaceutical package with the lubricous coating may be at least 10% greater than an uncoated glass pharmaceutical package.

CROSS REFERENCE TO RELATED APPLICATIONS

The present specification is a continuation of U.S. patent applicationSer. No. 15/331,120 filed Oct. 21, 2016 and entitled “Glass ContainersWith Improved Strength and Improved Damage Tolerance”, which is acontinuation of U.S. patent application Ser. No. 14/075,630 filed Nov.8, 2013 and entitled “Glass Containers with Improved Strength andImproved Damage Tolerance,” which claims priority to U.S. ProvisionalPatent Application Ser. No. 61/731,767 filed Nov. 30, 2012 and entitled“Glass Containers With Improved Attributes,” each of which isincorporated by reference herein in their entireties.

BACKGROUND Field

The present specification generally relates to glass containers and,more specifically, to glass containers for use in storing pharmaceuticalformulations.

Technical Background

Historically, glass has been used as the preferred material forpackaging pharmaceuticals because of its hermeticity, optical clarity,and excellent chemical durability relative to other materials.Specifically, the glass used in pharmaceutical packaging must haveadequate chemical durability so as to not affect the stability of thepharmaceutical formulations contained therein. Glasses having suitablechemical durability include those glass compositions within the ASTMstandard ‘Type IA’ and ‘Type IB’ glass compositions which have a provenhistory of chemical durability.

Although Type IA and Type IB glass compositions are commonly used inpharmaceutical packages, they do suffer from several deficiencies,including a tendency for the inner surfaces of the pharmaceuticalpackage to shed glass particulates or “delaminate” following exposure topharmaceutical solutions.

In addition, use of glass in pharmaceutical packaging may also belimited by the mechanical performance of the glass. Specifically, thehigh processing speeds utilized in the manufacture and filling of glasspharmaceutical packages may result in mechanical damage on the surfaceof the package, such as abrasions, as the packages come into contactwith processing equipment, handling equipment, and/or other packages.This mechanical damage significantly decreases the strength of the glasspharmaceutical package resulting in an increased likelihood that crackswill develop in the glass, potentially compromising the sterility of thepharmaceutical contained in the package or causing the complete failureof the package.

Accordingly, a need exists for alternative glass containers for use aspharmaceutical packages which exhibit a combination of at least two ofimproved resistance to delamination, increased strength, and/or damagetolerance.

SUMMARY

According to one embodiment, a glass container may include a body havingan inner surface, an outer surface and a wall thickness extendingbetween the outer surface and the inner surface. A compressivelystressed layer may extend from the outer surface of the body into thewall thickness. The compressively stressed layer may have a surfacecompressive stress greater than or equal to 150 MPa. A lubricous coatingmay be positioned around at least a portion of the outer surface of thebody. The outer surface of the body with the lubricous coating may havea coefficient of friction less than or equal to 0.7.

In another embodiment, a glass container may include a body having aninner surface, an outer surface and a wall thickness extending betweenthe outer surface and the inner surface. The body may be formed from aType 1, Class B glass according to ASTM Standard E438-92. Acompressively stressed layer may extend from the outer surface of thebody into the wall thickness. The compressively stressed layer may havea surface compressive stress greater than or equal to 150 MPa. Alubricous coating may be positioned around at least a portion of theouter surface of the body. The outer surface of the body with thelubricous coating may have a coefficient of friction less than or equalto 0.7.

Additional features and advantages of the embodiments of the glasscontainers described herein will be set forth in the detaileddescription which follows, and in part will be readily apparent to thoseskilled in the art from that description or recognized by practicing theembodiments described herein, including the detailed description whichfollows, the claims, as well as the appended drawings.

It is to be understood that both the foregoing general description andthe following detailed description describe various embodiments and areintended to provide an overview or framework for understanding thenature and character of the claimed subject matter. The accompanyingdrawings are included to provide a further understanding of the variousembodiments, and are incorporated into and constitute a part of thisspecification. The drawings illustrate the various embodiments describedherein, and together with the description serve to explain theprinciples and operations of the claimed subject matter.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 schematically depicts a cross section of a glass containeraccording to one or more embodiments described herein;

FIG. 2 schematically depicts a compressively stressed layer in a portionof the sidewall of the glass container of FIG. 1;

FIG. 3 schematically depicts a portion of the sidewall of the glasscontainer formed from laminated glass;

FIG. 4 schematically depicts a horizontal compression apparatus fortesting the horizontal compression strength of a glass container;

FIG. 5 schematically depicts a glass container having a barrier coatingpositioned on at least a portion of the inner surface of the glasscontainer, according to one or more embodiments shown and describedherein;

FIG. 6 schematically depicts a portion of a sidewall of a glasscontainer having a persistent layer homogeneity;

FIG. 7 schematically depicts a portion of a sidewall of a glasscontainer having a persistent surface homogeneity;

FIG. 8 schematically depicts a glass container with a lubricous coatingpositioned on the outer surface of the glass container;

FIG. 9 schematically depicts a testing jig for determining thecoefficient of friction between two glass containers;

FIG. 10 schematically depicts an apparatus for assessing the thermalstability of a coating applied to a glass container;

FIG. 11 graphically depicts the light transmittance data for coated anduncoated vials measured in the visible light spectrum from 400-700 nm,according to one or more embodiments shown and described herein;

FIG. 12A schematically depicts a tenacious organic lubricous coatingpositioned on the outer surface of a glass container according to one ormore embodiments shown and described herein;

FIG. 12B schematically depicts a tenacious organic lubricous coatingpositioned on the outer surface of a glass container according to one ormore embodiments shown and described herein;

FIG. 13 schematically depicts the chemical structure of a diaminemonomer which may be used to form a polyimide coating layer;

FIG. 14 schematically depicts the chemical structure of another diaminemonomer which may be used to form a polyimide coating layer;

FIG. 15 schematically depicts the chemical structures of some monomersthat may be used as polyimide coatings applied to glass containers;

FIG. 16 graphically depicts the effect of composition and temperature onvolatilization for a Type IB glass and a boron-free glass;

FIG. 17 schematically depicts the reaction steps of a silane bonding toa substrate, according to one or more embodiments shown and describedherein;

FIG. 18 schematically depicts the reaction steps of a polyimide bondingto a silane, according to one or more embodiments shown and describedherein;

FIG. 19 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for vials, according toone or more embodiments shown and described herein;

FIG. 20 contains a Table reporting the load and measured coefficient offriction for Type IB glass vials and vials formed from a Reference GlassComposition that were ion exchanged and coated, according to one or moreembodiments shown and described herein;

FIG. 21 graphically depicts the failure probability as a function ofapplied stress in four point bending for tubes formed from a ReferenceGlass Composition in as received condition, in ion exchanged condition(uncoated), in ion exchanged condition (coated and abraded), in ionexchanged condition (uncoated and abraded) and for tubes formed fromType IB glass in as received condition and in ion exchanged condition,according to one or more embodiments shown and described herein;

FIG. 22 schematically depicts gas chromatograph-mass spectrometer outputdata for a APS/Novastrat® 800 coating, according to one or moreembodiments shown and described herein;

FIG. 23 graphically depicts gas chromatography-mass spectrometer outputdata for a DC806A coating, according to one or more embodiments shownand described herein;

FIG. 24 is a Table reporting different lubricous coating compositionswhich were tested under lyophilization conditions, according to one ormore embodiments shown and described herein;

FIG. 25 is a chart reporting the coefficient of friction for bare glassvials and vials having a silicone resin coating tested in a vial-on-vialjig, according to one or more embodiments shown and described herein;

FIG. 26 is a chart reporting the coefficient of friction for vialscoated with an APS/PMDA-ODA (poly(4,4′-oxydiphenylene-pyromellitimide)polyimide coating and abraded multiple times under different appliedloads in a vial-on-vial jig, according to one or more embodiments shownand described herein;

FIG. 27 is a chart reporting the coefficient of friction for vialscoated with an APS coating and abraded multiple times under differentapplied loads in a vial-on-vial jig, according to one or moreembodiments shown and described herein;

FIG. 28 is a chart reporting the coefficient of friction for vialscoated with an APS/PMDA-ODA (poly(4,4′-oxydiphenylene-pyromellitimide)polyimide coating and abraded multiple times under different appliedloads in a vial-on-vial jig after the vials were exposed to 300° C. for12 hours, according to one or more embodiments shown and describedherein;

FIG. 29 is a chart reporting the coefficient of friction for vialscoated with an APS coating and abraded multiple times under differentapplied loads in a vial-on-vial jig after the vials were exposed to 300°C. for 12 hours, according to one or more embodiments shown anddescribed herein;

FIG. 30 is a chart reporting the coefficient of friction for Type IBvials coated with a PMDA-ODA (poly(4,4′-oxydiphenylene-pyromellitimide)polyimide coating and abraded multiple times under different appliedloads in a vial-on-vial jig, according to one or more embodiments shownand described herein;

FIG. 31 graphically depicts the coefficient of friction forAPS/Novastrat® 800 coated vials before and after lyophilization,according to one or more embodiments shown and described herein;

FIG. 32 graphically depicts the coefficient of friction forAPS/Novastrat® 800 coated vials before and after autoclaving, accordingto one or more embodiments shown and described herein;

FIG. 33 graphically depicts the coefficient of friction for coated glasscontainers exposed to different temperature conditions and for anuncoated glass container;

FIG. 34 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for vials, according toone or more embodiments shown and described herein;

FIG. 35 is a Table illustrating the change in the coefficient offriction with variations in the composition of the coupling agent of alubricous coating applied to a glass container as described herein;

FIG. 36 graphically depicts the coefficient of friction, applied forceand frictive force for coated glass containers before and afterdepyrogenation;

FIG. 37 graphically depicts the coefficient of friction, applied forceand frictive force for coated glass containers before and afterdepyrogenation, according to one or more embodiments shown and describedherein;

FIG. 38 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for vials, according toone or more embodiments shown and described herein;

FIG. 39 graphically depicts the coefficient of friction, applied forceand frictive force for coated glass containers before and afterdepyrogenation, according to one or more embodiments shown and describedherein;

FIG. 40 graphically depicts the coefficient of friction, applied forceand frictive force for coated glass containers for differentdepyrogenation conditions;

FIG. 41 graphically depicts the coefficient of friction after varyingheat treatment times, according to one or more embodiments shown anddescribed herein;

FIG. 42 graphically depicts the light transmittance data for coated anduncoated vials measured in the visible light spectrum from 400-700 nm,according to one or more embodiments shown and described herein;

FIG. 43 graphically depicts the coefficient of friction, applied forceand frictive force for coated glass containers before and afterdepyrogenation, according to one or more embodiments shown and describedherein;

FIG. 44 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for vials, according toone or more embodiments shown and described herein;

FIG. 45 is a micrograph of a coating, according to one or moreembodiments shown and described herein;

FIG. 46 is a micrograph of a coating, according to one or moreembodiments shown and described herein;

FIG. 47 is a micrograph of a coating, according to one or moreembodiments shown and described herein;

FIG. 48 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for theas-coated vials of a Comparative Example;

FIG. 49 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for thethermally treated vials of a Comparative Example;

FIG. 50 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for theas-coated vials of a Comparative Example;

FIG. 51 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for thethermally treated vials of a Comparative Example:

FIG. 52 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for vialswith an adhesion promoter layer in as-coated condition;

FIG. 53 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for vialswith an adhesion promoter layer in as-coated condition;

FIG. 54 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for vialswith an adhesion promoter layer after depyrogenation;

FIG. 55 graphically depicts the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for vialswith an adhesion promoter layer after depyrogenation;

FIG. 56 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for vials with an adhesionpromoter layer, according to one or more embodiments shown and describedherein; and

FIG. 57 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for vials with an adhesionpromoter layer, according to one or more embodiments shown and describedherein.

DETAILED DESCRIPTION

Reference will now be made in detail to embodiments of glass containers,examples of which are illustrated in the accompanying drawings. Wheneverpossible, the same reference numerals will be used throughout thedrawings to refer to the same or like parts. The glass containersdescribed herein have at least two performance attributes selected fromresistance to delamination, improved strength, and increased damageresistance. For example, the glass containers may have a combination ofresistance to delamination and improved strength; improved strength andincreased damage resistance; or resistance to delamination and increaseddamage resistance. In one particular embodiment, the glass containersdescribed herein have at least two performance attributes selected fromresistance to delamination, improved strength, and increased damageresistance. In one embodiment, a glass container may include a bodyhaving an inner surface, an outer surface and a wall thickness extendingbetween the outer surface and the inner surface. A compressivelystressed layer may extend from the outer surface of the body into thewall thickness. The compressively stressed layer may have a surfacecompressive stress greater than or equal to 150 MPa. A lubricous coatingmay be positioned around at least a portion of the outer surface of thebody. The outer surface of the body with the lubricous coating may havea coefficient of friction less than or equal to 0.7. Glass containerswith various combinations of resistance to delamination, improvedstrength, and increased damage resistance will be described in moredetail herein with specific reference to the appended drawings.

In the embodiments of the glass compositions described herein, theconcentration of constituent components (e.g., SiO₂, Al₂O₃, B₂O₃ and thelike) are specified in mole percent (mol. %) on an oxide basis, unlessotherwise specified.

The term “substantially free,” when used to describe the concentrationand/or absence of a particular constituent component in a glasscomposition, means that the constituent component is not intentionallyadded to the glass composition. However, the glass composition maycontain traces of the constituent component as a contaminant or tramp inamounts of less than 0.1 mol. %.

The term “chemical durability,” as used herein, refers to the ability ofthe glass composition to resist degradation upon exposure to specifiedchemical conditions. Specifically, the chemical durability of the glasscompositions described herein may be assessed according to threeestablished material testing standards: DIN 12116 dated March 2001 andentitled “Testing of glass—Resistance to attack by a boiling aqueoussolution of hydrochloric acid—Method of test and classification”; ISO695:1991 entitled “Glass—Resistance to attack by a boiling aqueoussolution of mixed alkali—Method of test and classification”; ISO720:1985 entitled “Glass—Hydrolytic resistance of glass grains at 121degrees C. —Method of test and classification”; and ISO 719:1985“Glass—Hydrolytic resistance of glass grains at 98 degrees C. —Method oftest and classification.” Each standard and the classifications withineach standard are described in further detail herein. Alternatively, thechemical durability of a glass composition may be assessed according toUSP <660> entitled “Surface Glass Test,” and or European Pharmacopeia3.2.1 entitled “Glass Containers For Pharmaceutical Use” which assessthe durability of the surface of the glass.

The term “strain point” and “T_(strain)” as used herein, refer to thetemperature at which the viscosity of the glass is 3×10¹⁴ poise.

The term “softening point,” as used herein, refers to the temperature atwhich the viscosity of the glass composition is 1×10⁷⁶ poise.

Conventional glass containers used for storing pharmaceuticals and/orother consumable products may experience damage during filling,packaging, and/or shipping. Such damage may be in the form of surfacescuffs, abrasions and/or scratches which, when sufficiently deep, mayresult in a through crack or even complete failure of the glasscontainer, thereby compromising the contents of the glass package.

In addition, some conventional glass containers may be susceptible todelamination, particularly when the glass container is formed fromalkali borosilicate glasses. Delamination refers to a phenomenon inwhich glass particles are released from the surface of the glassfollowing a series of leaching, corrosion, and/or weathering reactions.In general, the glass particles are silica-rich flakes of glass whichoriginate from the inner surface of the package as a result of theleaching of modifier ions into a solution contained within the package.These flakes may generally be from about 1 nm to about 2 microns (μm)thick with a width greater than about 50 μm. As these flakes areprimarily composed of silica, the flakes generally do not furtherdegrade after being released from the surface of the glass.

It has heretofore been hypothesized that delamination is due to phaseseparation which occurs in alkali borosilicate glasses when the glass isexposed to the elevated temperatures used for reforming the glass into acontainer shape.

However, it is now believed that the delamination of the silica-richglass flakes from the inner surfaces of the glass containers is due tothe compositional characteristics of the glass container immediatelyfollowing formation. Specifically, the high silica content of alkaliborosilicate glasses causes the glass to have relatively high meltingand forming temperatures. However, the alkali and borate components inthe glass composition melt and/or vaporize at much lower temperatures.In particular, the borate species in the glass are highly volatile andevaporate from the surface of the glass at the high temperaturesnecessary to form and reform the glass.

Specifically, glass stock is reformed into glass containers at hightemperatures and in direct flames. The high temperatures needed athigher equipment speeds cause the more volatile borate species toevaporate from portions of the surface of the glass. When thisevaporation occurs within the interior volume of the glass container,the volatilized borate species are re-deposited in other areas of theglass container surface causing compositional heterogeneities in theglass container surface, particularly with respect to the near-surfaceregions of the interior of the glass container (i.e., those regions ator directly adjacent to the inner surfaces of the glass container). Forexample, as one end of a glass tube is closed to form the bottom orfloor of the container, borate species may evaporate from the bottomportion of the tube and be re-deposited elsewhere in the tube. Theevaporation of material from the heel and floor portions of thecontainer is particularly pronounced as these areas of the containerundergo the most extensive re-formation and, as such, are exposed to thehighest temperatures. As a result, the areas of the container exposed tohigher temperatures may have silica-rich surfaces. Other areas of thecontainer which are amenable to boron deposition may have a boron-richlayer at the surface. Areas amenable to boron deposition which are at atemperature greater than the anneal point of the glass composition butless than the hottest temperature the glass is subjected to duringreformation can lead to boron incorporation on the surface of the glass.Solutions contained in the container may leach the boron from theboron-rich layer. As the boron-rich layer is leached from the glass, ahigh silica glass network (gel) remains which swells and strains duringhydration and eventually spalls from the surface.

The glass containers described herein mitigate at least two of theaforementioned problems. Specifically, the glass containers have atleast two performance attributes selected from resistance todelamination, improved strength, and increased damage resistance. Forexample, the glass containers may have a combination of resistance todelamination and improved strength; improved strength and increaseddamage resistance; or resistance to delamination and increased damageresistance. Each performance attribute and methods for achieving theperformance attribute will be described in further detail herein.

Referring now to FIGS. 1 and 2, one embodiment of a glass container 100for storing a pharmaceutical formulation is schematically depicted incross section. The glass container 100 generally comprises a body 102.The body 102 extends between an inner surface 104 and an outer surface106 and generally encloses an interior volume 108. In the embodiment ofthe glass container 100 shown in FIG. 1, the body 102 generallycomprises a wall portion 110 and a floor portion 112. The wall portion110 transitions into the floor portion 112 through a heel portion 114.The body 102 has a wall thickness T_(W) which extends between the innersurface 104 to the outer surface 106, as depicted in FIG. 1.

While the glass container 100 is depicted in FIG. 1 as having a specificshape form (i.e., a vial), it should be understood that the glasscontainer 100 may have other shape forms, including, without limitation,Vacutainers®, cartridges, syringes, ampoules, bottles, flasks, phials,tubes, beakers, or the like. Further, it should be understood that theglass containers described herein may be used for a variety ofapplications including, without limitation, as pharmaceutical packages,beverage containers, or the like.

Strength

Still referring to FIGS. 1 and 2, in some embodiments described herein,the body 102 includes a compressively stressed layer 202 extending fromat least the outer surface 106 of the body 102 into the wall thicknessT_(W) to a depth of layer DOL from the outer surface 106 of the body102. The compressively stressed layer 202 generally increases thestrength of the glass container 100 and also improves the damagetolerance of the glass container. Specifically, a glass container havinga compressively stressed layer 202 is generally able to withstand agreater degree of surface damage, such as scratches, chips, or the like,without failure compared to a non-strengthened glass container as thecompressively stressed layer 202 mitigates the propagation of cracksfrom surface damage in the compressively stressed layer 202.

In the embodiments described herein the depth of layer of thecompressively stressed layer may be greater than or equal to about 3 μm.In some embodiments, the depth of layer may be greater than 10 μm oreven greater than 20 μm. In some embodiments, the depth of layer may begreater than or equal to about 25 μm or even greater than or equal toabout 30 μm. For example, in some embodiments, the depth of layer may begreater than or equal to about 25 μm and up to about 150 μm. In someother embodiments, the depth of layer may be greater than or equal toabout 30 μm and less than or equal to about 150 μm. In yet otherembodiments, the depth of layer may be greater than or equal to about 30μm and less than or equal to about 80 μm. In some other embodiments, thedepth of layer may be greater than or equal to about 35 μm and less thanor equal to about 50 μm.

The compressively stressed layer 202 generally has a surface compressivestress (i.e., a compressive stress as measured at the outer surface 106)of greater than or equal to 150 MPa. In some embodiments, the surfacecompressive stress may be greater than or equal to 200 MPa, or evengreater than or equal to 250 MPa. In some embodiments, the surfacecompressive stress may be greater than or equal to 300 MPa, or evengreater than or equal to 350 MPa. For example, in some embodiments, thesurface compressive stress may be greater than or equal to about 300 MPaand less than or equal to about 750 MPa. In some other embodiments, thesurface compressive stress may be greater than or equal to about 400 MPaand less than or equal to about 700 MPa. In still other embodiments, thesurface compressive stress may be greater than or equal to about 500 MPaand less than or equal to about 650 MPa. The stress in ion-exchangedglass articles can be measured with an FSM (Fundamental Stress Meter)instrument. This instrument couples light into and out of thebirefringent glass surface. The measured birefringence is then relatedto stress through a material constant, the stress-optic or photoelasticcoefficient (SOC or PEC). Two parameters are obtained: the maximumsurface compressive stress (CS) and the exchange depth of layer (DOL).Alternatively, the compressive stress and depth of layer may be measuredusing refractive near field stress measurement techniques.

While the compressively stressed layer 202 has been shown and describedherein as extending from the outer surface 106 into the thickness T_(W)of the body 102, it should be understood that, in some embodiments, thebody 102 may further comprise a second compressively stressed layerwhich extends from the inner surface 104 into the thickness T_(W) of thebody 102. In this embodiment, the depth of layer and surface compressivestress of the second compressively stressed layer may mirror those ofthe compressively stressed layer 202 about the centerline of thethickness T_(W) of the body 102.

Several different techniques may be utilized to form the compressivelystressed layer 202 in the body 102 of the glass container 100. Forexample, in embodiments where the body 102 is formed from ionexchangeable glass, the compressively stressed layer 202 may be formedin the body 102 by ion exchange. In these embodiments, the compressivelystressed layer 202 is formed by placing the glass container in a bath ofmolten salt to facilitate the exchange of relatively large ions in themolten salt for relatively smaller ions in the glass. Several differentexchange reactions may be utilized to achieve the compressively stressedlayer 202. In one embodiment, the bath may contain molten KNO₃ saltwhile the glass from which the glass container 100 is formed containslithium and/or sodium ions. In this embodiment, the potassium ions inthe bath are exchanged for the relatively smaller lithium and/or sodiumions in the glass, thereby forming the compressively stressed layer 202.In another embodiment, the bath may contain NaNO₃ salt and the glassfrom which the glass container 100 is formed contains lithium ions. Inthis embodiment, the sodium ions in the bath are exchanged for therelatively smaller lithium ions in the glass, thereby forming thecompressively stressed layer 202.

In one specific embodiment, the compressively stressed layer 202 may beformed by submerging the glass container in a molten salt bath of 100%KNO₃ or, in the alternative, a mixture of KNO₃ and NaNO₃. For example,in one embodiment the molten salt bath may include KNO₃ with up to about10% NaNO₃. In this embodiment, the glass from which the container isformed may include sodium ions and/or lithium ions. The temperature ofthe molten salt bath may be greater than or equal to 350° C. and lessthan or equal to 500° C. In some embodiments, the temperature of themolten salt bath may be greater than or equal to 400° C. and less thanor equal to 500° C. In still other embodiments, the temperature of themolten salt bath may be greater than or equal to 450° C. and less thanor equal to 475° C. The glass container may be held in the molten saltbath for a time period sufficient to facilitate the exchange of therelatively large ions in the salt bath with relatively smaller ions inthe glass and thereby achieve the desired surface compressive stress anddepth of layer. For example, the glass may be held in the molten saltbath for a period of time which is greater than or equal to 0.05 hoursto less than or equal to about 20 hours in order to achieve the desireddepth of layer and surface compressive stress. In some embodiments theglass container may be held in the molten salt bath for greater than orequal to 4 hours and less than or equal to about 12 hours. In otherembodiments, the glass container may be held in the molten salt bath forgreater than or equal to about 5 hours and less than or equal to about 8hours. In one exemplary embodiment, the glass container may be ionexchanged in a molten salt bath which comprises 100% KNO₃ at atemperature greater than or equal to about 400° C. and less than orequal to about 500° C. for a time period greater than or equal to about5 hours and less than or equal to about 8 hours.

Typically, the ion exchange process is performed at temperatures morethan 150° C. below the strain point (T_(strain)) of the glass in orderto minimize stress relaxation due to elevated temperatures. However, insome embodiments, the compressively stressed layer 202 is formed in amolten salt bath which is at temperature greater than the strain pointof the glass. This type of ion exchange strengthening is referred toherein as “high temperature ion-exchange strengthening.” In hightemperature ion-exchange strengthening, relatively smaller ions in theglass are exchanged with relatively larger ions from the molten saltbath, as described above. As the relatively smaller ions are exchangedfor relatively larger ions at temperatures above the strain point, theresultant stress is released or “relaxed”. However, the replacement ofsmaller ions in the glass with larger ions creates a surface layer inthe glass which has a lower coefficient of thermal expansion (CTE) thanthe remainder of the glass. As the glass cools, the CTE differentialbetween the surface of the glass and the remainder of the glass createsthe compressively stressed layer 202. This high temperature ion-exchangetechnique is particularly well suited to strengthening glass articles,such as glass containers, which have complex geometries and typicallyreduces the strengthening process time relative to typical ion exchangeprocesses and also enables a greater depth of layer.

Still referring to FIGS. 1 and 2, in an alternative embodiment, thecompressively stressed layer 202 may be introduced into the body 102 ofthe glass container 100 by thermal tempering. Compressively stressedlayers are formed through thermal tempering by heating the glasscontainer and differentially cooling the surface of the glass relativeto the bulk of the glass. Specifically, a glass which is rapidly cooledhas a greater molar volume (or lower density) than a more slowly cooledglass. Accordingly, if the surface of the glass is intentionally rapidlycooled, the surface of the glass will have a larger volume and theinterior of the glass (i.e., the remainder of the glass below the outersurface) will necessarily cool at a slower rate as the heat must escapefrom the bulk through the surface. By creating a continuous gradient inmolar volume (or thermal history/density) from the outer surface 106into the wall thickness T_(W) of the body 102, a compressively stressedlayer 202 is produced which has a parabolic stress profile (i.e., thecompressive stress decreases parabolically with increasing distance fromthe outer surface 106 of the body 102). Thermal tempering processes aregenerally faster and less expensive than ion-exchange processes.However, the surface compressive stresses due to thermal temperingprocesses are generally lower than the surface compressive stresses dueto ion-exchange processes. In embodiments where the glass container isthermally tempered, the resultant compressively stressed layer extendsfrom the outer surface 106 to a depth of layer DOL which is up to 22% ofthe wall thickness T_(W) of the glass containers. For example, in someembodiments, the DOL may be from about 5% to about 22% of the wallthickness T_(W) or even from about 10% to about 22% of the wallthickness T_(W).

In a typical thermal tempering process, the glass container 100 is firstheated to its softening point and, thereafter, the outer surface 106 ofthe body 102 is rapidly cooled to below the softening point with afluid, such as with a gas jet or the like, to create a temperaturedifferential between the outer surface 106 of the body 102 and theremainder of the body 102, as described above. The temperaturedifferential between the outer surface 106 and the remainder of the bodyproduces a compressively stressed layer 202 extending into the wallthickness T_(W) of the body 102 from the outer surface 106. For example,the glass may be initially heated to 50-150° C. above its softeningpoint and thereafter rapidly cooled to room temperature by directing afluid onto the glass. The fluid may include, without limitation, air,oil, or oil-based fluids.

Referring now to FIGS. 1-3, in another embodiment, the glass container100 may be formed from laminated glass tubing which facilitates theformation of a compressively stressed layer 202 in at least the outersurface 106 of the body 102. The laminated glass generally comprises aglass core layer 204 and at least one glass cladding layer 206 a. In theembodiment of the glass container 100 depicted in FIG. 3, the laminatedglass includes a pair of glass cladding layers 206 a, 206 b. In thisembodiment, the glass core layer 204 generally comprises a first surface205 a and a second surface 205 b which is opposed to the first surface205 a. A first glass cladding layer 206 a is fused to the first surface205 a of the glass core layer 204 and a second glass cladding layer 206b is fused to the second surface 205 b of the glass core layer 204. Theglass cladding layers 206 a, 206 b are fused to the glass core layer 204without any additional materials, such as adhesives, coating layers orthe like, disposed between the glass core layer 204 and the glasscladding layers 206 a, 206 b.

In the embodiment shown in FIG. 3, the glass core layer 204 is formedfrom a first glass composition having an average core coefficient ofthermal expansion CTE_(core) and the glass cladding layers 206 a, 206 bare formed from a second, different glass composition which has anaverage coefficient of thermal expansion CTE_(clad). In the embodimentsdescribed herein, CTE_(core) is not equal to CTE_(clad) such that acompressive stress layer is present in at least one of the core layer orthe cladding layer. In some embodiments, CTE_(core) is greater thanCTE_(clad) which results in the glass cladding layers 206 a, 206 b beingcompressively stressed without being ion exchanged or thermallytempered. In some other embodiments, such as when the laminate glasscomprises a single core layer and a single cladding layer, CTE_(c1ad)may be greater than CTE_(core) which results in the glass core layerbeing compressively stressed without being ion exchanged or thermallytempered.

The laminated glass tubing from which the glass container is formed maybe formed as described in U.S. Pat. No. 4,023,953, which is incorporatedherein by reference. In embodiments, the glass forming the glass corelayer 204 is formed from a glass composition which has an averagecoefficient of thermal expansion CTE_(core) that is greater than theaverage coefficient of thermal expansion CTE_(clad) of either of theglass cladding layers 206 a, 206 b. As the glass core layer 204 and theglass cladding layers 206 a, 206 b cool, the difference in the averagecoefficients of thermal expansion of the glass core layer 204 and theglass cladding layers 206 a, 206 b cause a compressively stressed layerto develop in the glass cladding layers 206 a, 206 b. When the laminatedglass is used to form a container, these compressively stressed layersextend from the outer surface 106 of the glass container 100 into thewall thickness T_(W) and form the inner surface 104 of the glasscontainer into the wall thickness T_(W). In some embodiments, thecompressively stressed layer may extend from the outer surface of thebody of the glass container into the wall thickness T_(W) to a depth oflayer which is from about 1 μm to about 90% of the wall thickness T_(W).In some other embodiments, the compressively stressed layer may extendfrom the outer surface of the body of the glass container into the wallthickness T_(W) to a depth of layer which is from about 1 μm to about33% of the wall thickness T_(W). In still other embodiments, thecompressively stressed layer may extend from the outer surface of thebody of the glass container into the wall thickness T_(W) to a depth oflayer which is from about 1 μm to about 10% of the wall thickness T_(W).

After the laminated tube is formed, the tube may be formed into acontainer shape using conventional tube conversion techniques.

In some embodiments where the glass container is formed from laminatedglass, the at least one cladding layer forms the inner surface of thebody of the glass container such that the at least one glass claddinglayer is in direct contact with product stored in the glass container.In these embodiments, the at least one cladding layer may be formed froma glass composition which is resistant to delamination, as described infurther detail herein. Accordingly, it should be understood that the atleast one cladding layer may have a delamination factor of less than orequal to 10, as described in further detail herein.

In another alternative embodiment, the glass container may bestrengthened by applying a coating to the glass body. For example, acoating of an inorganic material, such as titania, may be applied to atleast a portion of the outer surface of the glass body either by sootdeposition or by vapor deposition processes. The titania coating has alower coefficient of thermal expansion than the glass it is beingdeposited on. As the coating and the glass cool, the titania shrinksless than the glass and, as a result, the surface of the glass body isin tension. In these embodiments, it should be understood that thesurface compressive stress and depth of layer are measured from thesurface of the coating rather than the surface of the coated glass body.While the inorganic coating material has been described herein ascomprising titania, it should be understood that other inorganic coatingmaterials with suitably low coefficients of thermal expansion are alsocontemplated. In embodiments, the inorganic coating may have acoefficient of friction of less than 0.7 relative to a like coatedcontainer. The inorganic coating may also be thermally stable attemperatures greater than or equal to 250° C., as described furtherherein.

In another alternative embodiment, the glass body can be strengthened bythe glass body with a high modulus coating having a coefficient ofthermal expansion equal to or greater than the underlying glass body.Strengthening is achieved by the difference in elastic modulus impartingdamage resistance while the difference in thermal expansion imparts acompressive stress in the glass surface (balancing tension in the highmodulus coating). In these embodiments, it should be understood that thesurface compressive stress and depth of layer are measured from thesurface of the glass body rather than the surface of the coated glassbody. The high modulus makes it difficult for scratches and damage to beintroduced and the underlying compressive layer prevents scratches andflaws from propagating. An exemplary material pairing to demonstratethis effect is a sapphire coating on 33 expansion borosilicate glass ora zirconium oxide coating deposited on 51 expansion borosilicate glass.

Based on the foregoing, it should be understood that, in someembodiments, the glass containers may include a compressively stressedlayer which extends from at least the outer surface of the body into thewall thickness of the glass container. The compressively stressed layerimproves the mechanical strength of the glass container relative to aglass container which does not include a compressively stressed layer.The compressively stressed layer also improves the damage tolerance ofthe glass container such that the glass container is able to withstandgreater surface damage (i.e., scratches, chips, etc., which extenddeeper into the wall thickness of the glass container) without failurerelative to a glass container which does not include a compressivelystressed layer. Further, it should also be understood that, in theseembodiments, the compressively stressed layer may be formed in the glasscontainer by ion exchange, by thermal tempering, by forming the glasscontainer from laminated glass, or by applying a coating to the glassbody. In some embodiments, the compressively stressed layer may beformed by a combination of these techniques.

Delamination Resistance

In some embodiments, the glass containers 100 may also resistdelamination following long term exposure to certain chemicalcompositions stored in the container. As noted above, delamination mayresult in the release of silica-rich glass flakes into a solutioncontained within the glass container after extended exposure to thesolution. Accordingly, the resistance to delamination may becharacterized by the number of glass particulates present in a solutioncontained within the glass container after exposure to the solutionunder specific conditions. In order to assess the long-term resistanceof the glass container to delamination, an accelerated delamination testis utilized. The test may be performed on both ion-exchanged andnon-ion-exchanged glass containers. The test consists of washing theglass container at room temperature for 1 minute and depyrogenating thecontainer at about 320° C. for 1 hour. Thereafter a solution of 20 mMglycine with a pH of 10 in water is placed in the glass container to80-90% fill, the glass container is closed, and the glass container israpidly heated to 100° C. and then heated from 100° C. to 121° C. at aramp rate of 1 deg/min at a pressure of 2 atmospheres. The glasscontainer and solution are held at this temperature for 60 minutes,cooled to room temperature at a rate of 0.5 deg./min and the heatingcycle and hold are repeated. The glass container is then heated to 50°C. and held for ten or more days for elevated temperature conditioning.After heating, the glass container is dropped from a distance of atleast 18″ onto a firm surface, such as a laminated tile floor, todislodge any flakes or particles that are weakly adhered to the innersurface of the glass container. The distance of the drop may be scaledappropriately to prevent larger sized vials from fracturing on impact.

Thereafter, the solution contained in the glass container is analyzed todetermine the number of glass particles present per liter of solution.Specifically, the solution from the glass container is directly pouredonto the center of a Millipore Isopore Membrane filter (Millipore#ATTP02500 held in an assembly with parts #AP1002500 and #M000025A0)attached to vacuum suction to draw the solution through the filterwithin 10-15 seconds for 5 mL. Thereafter, another 5 mL of water is usedas a rinse to remove buffer residue from the filter media. Particulateflakes are then counted by differential interference contrast microscopy(DIC) in the reflection mode as described in “Differential interferencecontrast (DIC) microscopy and modulation contrast microscopy” fromFundamentals of light microscopy and digital imaging. New York:Wiley-Liss, pp 153-168. The field of view is set to approximately 1.5mm×1.5 mm and particles larger than 50 μm are counted manually. Thereare 9 such measurements made in the center of each filter membrane in a3×3 pattern with no overlap between images. If larger areas of thefilter media are analyzed, results can be normalized to equivalent area(i.e., 20.25 mm²). The images collected from the optical microscope areexamined with an image analysis program (Media Cybernetic's ImageProPlus version 6.1) to measure and count the number of glass flakespresent. This is accomplished as follows: all of the features within theimage that appeared darker than the background by simple grayscalesegmentation are highlighted; the length, width, area, and perimeter ofall of the highlighted features that have a length greater than 25micrometers are then measured; any obviously non-glass particles arethen removed from the data; the measurement data is then exported into aspreadsheet. Then, all of the features greater than 25 micrometers inlength and brighter than the background are extracted and measured; thelength, width, area, perimeter, and X-Y aspect ratio of all of thehighlighted features that have a length greater than 25 micrometers aremeasured; any obviously non-glass particles are removed from the data;and the measurement data is appended to the previously exported data inthe spreadsheet. The data within the spreadsheet is then sorted byfeature length and broken into bins according to size. The reportedresults are for features greater than 50 micrometers in length. Each ofthese groups is then counted and the counts reported for each of thesamples.

A minimum of 100 mL of solution is tested. As such, the solution from aplurality of small containers may be pooled to bring the total amount ofsolution to 100 mL. For containers having a volume greater than 10 mL,the test is repeated for a trial of 10 containers formed from the sameglass composition under the same processing conditions and the result ofthe particle count is averaged for the 10 containers to determine anaverage particle count. Alternatively, in the case of small containers,the test is repeated for a trial of 10 vials, each of which is analyzedand the particle count averaged over the multiple trials to determine anaverage particle count per trial. Averaging the particle count overmultiple containers accounts for potential variations in thedelamination behavior of individual containers. Table 1 summarizes somenon-limiting examples of sample volumes and numbers of containers fortesting:

TABLE 1 Table of Exemplary Test Specimens Minimum Total Nominal VialVial Max Solution Number of Solution Capacity Volume per Vial Vials inNumber of Tested (mL) (mL) (mL) a Trial Trials (mL) 2.0 4.0 3.2 10 4 1283.5 7.0 5.6 10 2 112 4.0 6.0 4.8 10 3 144 5.0 10.0 8.0 10 2 160 6.0 10.08.0 10 2 160 8.0 11.5 9.2 10 2 184 10.0 13.5 10.8 10 1 108 20.0 26.020.8 10 1 208 30.0 37.5 30.0 10 1 300 50.0 63.0 50.4 10 1 504

It should be understood that the aforementioned test is used to identifyparticles which are shed from the interior wall(s) of the glasscontainer due to delamination and not tramp particles present in thecontainer from forming processes or particles which precipitate from thesolution enclosed in the glass container as a result of reactionsbetween the solution and the glass. Specifically, delamination particlesmay be differentiated from tramp glass particles based on the aspectratio of the particle (i.e., the ratio of the maximum length of theparticle to the thickness of the particle, or a ratio of the maximum andminimum dimensions). Delamination produces particulate flakes orlamellae which are irregularly shaped and typically have a maximumlength greater than about 50 μm but often greater than about 200 μm. Thethickness of the flakes is usually greater than about 100 nm and may beas large as about 1 μm. Thus, the minimum aspect ratio of the flakes istypically greater than about 50. The aspect ratio may be greater thanabout 100 and sometimes greater than about 1000. In contrast, trampglass particles will generally have a low aspect ratio which is lessthan about 3. Accordingly, particles resulting from delamination may bedifferentiated from tramp particles based on aspect ratio duringobservation with the microscope. Other common non-glass particlesinclude hairs, fibers, metal particles, plastic particles, and othercontaminants and are thus excluded during inspection. Validation of theresults can be accomplished by evaluating interior regions of the testedcontainers. Upon observation, evidence of skin corrosion/pitting/flakeremoval, as described in “Nondestructive Detection of Glass Vial InnerSurface Morphology with Differential Interference Contrast Microscopy”from Journal of Pharmaceutical Sciences 101(4), 2012, pages 1378-1384,is noted.

The number of particles present following accelerated delaminationtesting may be utilized to establish a delamination factor for the setof vials tested. Trials of glass containers which average less than 10glass particles with a minimum length of about 50 μm and an aspect ratioof greater than about 50 per trial following accelerated delaminationtesting are considered to have a delamination factor of 10. Trials ofglass containers which average less than 9 glass particles with aminimum length of about 50 μm and an aspect ratio of greater than about50 per trial following accelerated delamination testing are consideredto have a delamination factor of 9. Trials of glass containers whichaverage less than 8 glass particles with a minimum length of about 50 μmand an aspect ratio of greater than about 50 per trial followingaccelerated delamination testing are considered to have a delaminationfactor of 8. Trials of glass containers which average less than 7 glassparticles with a minimum length of about 50 μm and an aspect ratio ofgreater than about 50 per trial following accelerated delaminationtesting are considered to have a delamination factor of 7. Trials ofglass containers which average less than 6 glass particles with aminimum length of about 50 μm and an aspect ratio of greater than about50 per trial following accelerated delamination testing are consideredto have a delamination factor of 6. Trials of glass containers whichaverage less than 5 glass particles with a minimum length of about 50 μmand an aspect ratio of greater than about 50 per trial followingaccelerated delamination testing are considered to have a delaminationfactor of 5. Trials of glass containers which average less than 4 glassparticles with a minimum length of about 50 μm and an aspect ratio ofgreater than about 50 per trial following accelerated delaminationtesting are considered to have a delamination factor of 4. Trials ofglass containers which average less than 3 glass particles with aminimum length of about 50 μm and an aspect ratio of greater than about50 per trial following accelerated delamination testing are consideredto have a delamination factor of 3. Trials of glass containers whichaverage less than 2 glass particles with a minimum length of about 50 μmand an aspect ratio of greater than about 50 per trial followingaccelerated delamination testing are considered to have a delaminationfactor of 2. Trials of glass containers which average less than 1 glassparticle with a minimum length of about 50 μm and an aspect ratio ofgreater than about 50 per trial following accelerated delaminationtesting are considered to have a delamination factor of 1. Trials ofglass containers which have 0 glass particles with a minimum length ofabout 50 μm and an aspect ratio of greater than about 50 per trialfollowing accelerated delamination testing are considered to have adelamination factor of 0. Accordingly, it should be understood that thelower the delamination factor, the better the resistance of the glasscontainer to delamination. In some embodiments described herein, atleast the inner surface of the body of the glass container has adelamination factor of 10 or lower (e.g., a delamination factor of 3, 2,1 or 0). In some other embodiments, the entire body of the glasscontainer, including both the inner surface and the outer surface, has adelamination factor of 10 or lower (e.g., a delamination factor of 3, 2,1, or 0).

In some embodiments, a glass container having a delamination factor of10 or lower may be obtained by forming the glass container with abarrier coating on the inner surface of the body such that the barriercoating is the inner surface of the body. Referring to FIG. 5 by way ofexample, a glass container 100 with a barrier coating 131 deposited onat least a portion of the inner surface 104 of the body 102 isschematically depicted. The barrier coating 131 does not delaminate orotherwise degrade and prevents product stored in the interior volume 108of the glass container 100, such as pharmaceutical compositions or thelike, from contacting the inner surface 104 of the body 102 therebymitigating delamination of the glass container. The barrier coating isgenerally non-permeable to aqueous solutions, is insoluble in water, andhydrolytically stable.

In some embodiments described herein, the barrier coating 131 is atenacious inorganic coating that is permanently adhered to the innersurface 104 of the glass container 100. The barrier coating 131 may be ametal nitride coating, a metal oxide coating, a metal sulfide coating,SiO₂, diamond-like carbide, graphenes or a carbide coating. For example,in some embodiments, the tenacious inorganic coating may be formed fromat least one metal oxide such as Al₂O₃, TiO₂, ZrO₂, SnO, SiO₂, Ta₂O₅,Nb₂O₅, Cr₂O₃, V₂O₅, ZnO, or HfO₂. In some other embodiments, thetenacious inorganic coating may be formed from a combination of two ormore of metal oxides such as Al₂O₃, TiO₂, ZrO₂, SnO, SiO₂, Ta₂O₅, Nb₂O₅,Cr₂O₃, V₂O₅, ZnO, or HfO₂. In some other embodiments, the barriercoating 131 may comprise a first layer of a first metal oxide depositedon the inner surface of the glass container and a second layer of asecond metal oxide deposited over the first layer. In these embodiments,the barrier coating 131 may be deposited using a variety of depositiontechniques including, without limitation, atomic layer deposition,chemical vapor deposition, physical vapor deposition, and the like.Alternatively, the barrier coating may be applied with one or moreliquid application techniques such as dip coating, spray coating orplasma coating. Spray coating techniques may include high volume lowpressure (HVLP) and low volume low pressure (LVLP) spray coating,electrostatic spray coating, airless spray coating, ultrasonicatomization with airless spray coating, aerosol jet coating, and ink jetcoating. Plasma coating techniques may include standard primary andsecondary plasma coating, microwave assisted plasma coating, andatmospheric plasma coating and the like.

While embodiments of the barrier coating 131 have been described hereinas comprising inorganic materials, it should be understood that, in someembodiments, the barrier coating 131 may be an organic coating. Forexample, in embodiments where the barrier coating 131 is an organiccoating, the organic coating may comprise polybenzimidazoles,polybisoxazoles, polybisthiazoles, polyetherimides, polyquinolines,polythiophenes, phenylene sulfides, polysulfones, polycyanurates,parylenes, fluorinated polyolefins including polytetrafluorethylenes andother fluoro-substituted polyolefins, perfluoroalkoxy polymers,polyether ether ketones (PEEK), polyamides, epoxies, polyphenolics,polyurethane acrylates, cyclic olefin copolymer and cyclic olefinpolymers, polyolefins including polyethylenes, oxidized polyethylenes,polypropylenes, polyethylene/propylene copolymers, polyethylene/vinylacetate copolymers, polyvinylchloride, polyacrylates, polymethacrylates,polystyrenes, polyterpenes, polyanhydrides, polymaleicanhydrides,polyformaldehydes, polyacetals and copolymers of polyacetals,polysiloxanes of dimethyl or diphenyl or methyl/phenyl mixtures,perfluorinated siloxanes and other substituted siloxanes, polyimides,polycarbonates, polyesters, parafins and waxes, or various combinationsthereof. In some embodiments, the organic coating used as a barriercoating 131 may include polysiloxanes of dimethyl, diphenyl, ormethyl/phenyl mixtures. Alternatively, the organic coating may be apolycarbonate or polyethylene terephthalate. In some embodiments, thebarrier coating 131 may be formed from a layered structure comprisingone or more of the aforementioned polymers and/or copolymers.

Barrier coatings may be utilized in conjunction with glass containersformed from any glass composition. However, barrier coatings areparticularly well suited for use with glass containers formed from glasscompositions which do not exhibit a resistance to delamination uponformation into a glass container. Such glass compositions may include,without limitation, those glass compositions designated as Type I ClassA, Type I Class B, and Type II glass compositions according to ASTMStandard E438-92 (2011) entitled “Standard Specification for Glasses inLaboratory Apparatus.” Such glass compositions may have the requisitechemical durability under the ASTM Standard, but do not exhibitresistance to delamination. For example, Table 2 below lists severalnon-limiting examples of Type I Class B glass compositions which do notexhibit a resistance to delamination. As such, barrier coatings asdescribed herein may be used on at least the inner surfaces ofcontainers formed from these compositions such that the container has adelamination factor of 10 or lower.

TABLE 2 Exemplary Type I, Class B Glass Compositions Example 1 Example 2Example 3 (wt. %) (wt. %) (wt. %) SiO₂ 71.70 74.60 70.10 Al₂O₃ 6.61 5.563.41 B₂O₃ 11.50 10.90 12.40 Na₂O 6.40 6.93 5.91 K₂O 2.35 0.04 2.80 MgO0.300 0.057 0.009 CaO 0.56 1.47 1.03 SrO 0.004 0.004 0.026 BaO 0.0030.003 2.73 ZnO 0.000 0.000 0.97 Fe₂O₃ 0.092 0.046 0.049 TiO₂ 0.028 0.0180.027 ZrO₂ 0.033 0.032 0.038 As₂O₅ 0.0003 0.0828 0.0003 Cl 0.0450 0.00200.0750

In some alternative embodiments, a glass container having a delaminationfactor of 10 or lower is achieved by forming the glass container suchthat the glass container has homogenous compositional characteristicswhich, in turn, reduces the susceptibility of the glass container todelamination, as described in copending U.S. patent application Ser. No.13/912,457 filed Jun. 7, 2013 entitled “Delamination Resistant GlassContainers” and assigned to Corning Incorporated. Specifically, it isbelieved that delamination of the glass container may be due, at leastin part, to heterogeneities in the glass composition in at least theinterior of the glass container, as described above. Minimizing suchcompositional heterogeneities produces a glass container which has adelamination factor of 10 or lower.

Referring now to FIGS. 1 and 6, in some embodiments, the glasscontainers described herein have a homogenous composition through thethickness of the glass body 102 in each of the wall, heel, and floorportions such that at least the inner surface 104 of the body has adelamination factor of 10 or lower. Specifically, FIG. 6 schematicallydepicts a partial cross section of a wall portion 110 of the glasscontainer 100. The glass body 102 of the glass container 100 has aninterior region 120 which extends from about 10 nm below the innersurface 104 of the glass container 100 (indicated in FIG. 6 as D_(LR1))into the thickness of the wall portion 110 to a depth D_(LR2) from theinner surface 104 of the glass container. The interior region extendingfrom about 10 nm below the inner surface 104 is differentiated from thecomposition in the initial 5-10 nm below the surface due to experimentalartifacts. At the start of a dynamic secondary ion mass spectroscopy(DSIMS) analysis to determine the composition of the glass, the initial5-10 nm is not included in the analysis because of three concerns:variable sputtering rate of ions from the surface as a result ofadventitious carbon, establishment of a steady state charge in part dueto the variable sputtering rate, and mixing of species whileestablishing a steady state sputtering condition. As a result, the firsttwo data points of the analysis are excluded. Accordingly, it should beunderstood that the interior region 120 has a thickness T_(LR) which isequal to D_(LR2)−D_(LR1). The glass composition within the interiorregion has a persistent layer homogeneity which, in conjunction with thethickness T_(LR) of the interior region, is sufficient to preventdelamination of the glass body following long term exposure to asolution contained in the interior volume of the glass container. Insome embodiments, the thickness T_(LR) is at least about 100 nm. In someembodiments, the thickness T_(LR) is at least about 150 nm. In someother embodiments, the thickness T_(LR) is at least about 200 nm or evenabout 250 nm. In some other embodiments, the thickness T_(LR) is atleast about 300 nm or even about 350 nm. In yet other embodiments, thethickness T_(LR) is at least about 500 nm. In some embodiments, theinterior region 120 may extend to a thickness T_(LR) of at least about 1μm or even at least about 2 μm.

While the interior region is described herein as extending from 10 nmbelow the inner surface 104 of the glass container 100 into thethickness of the wall portion 110 to a depth D_(LR2) from the innersurface 104 of the glass container, it should be understood that otherembodiments are possible. For example, it is hypothesized that, despitethe experimental artifacts noted above, the interior region with thepersistent layer homogeneity may actually extend from the inner surface104 of the glass container 100 into the thickness of the wall portion.Accordingly, in some embodiments, the thickness T_(LR) may extend fromthe inner surface 104 to the depth D_(LR2). In these embodiments, thethickness T_(LR) may be at least about 100 nm. In some embodiments, thethickness T_(LR) is at least about 150 nm. In some other embodiments,the thickness T_(LR) is at least about 200 nm or even about 250 nm. Insome other embodiments, the thickness T_(LR) is at least about 300 nm oreven about 350 nm. In yet other embodiments, the thickness T_(LR) is atleast about 500 nm. In some embodiments, the interior region 120 mayextend to a thickness T_(LR) of at least about 1 μm or even at leastabout 2 μm.

In embodiments where the glass container is formed such that the glasscontainer has a persistent layer homogeneity, the phrase “persistentlayer homogeneity” means that the concentration of the constituentcomponents (e.g., SiO₂, Al₂O₃, Na₂O, etc.) of the glass composition inthe interior region do not vary from the concentration of the sameconstituent components at the midpoint of a thickness of the glass layerwhich contains the interior region by an amount which would result indelamination of the glass body upon long term exposure to a solutioncontained within the glass container. For example, in embodiments wherethe glass container is formed from a single glass composition, the glassbody contains a single layer of glass and the concentration ofconstituent components in the interior region is compared to theconcentration of the same components at a point along the midpoint lineMP which evenly bisects the glass body between the inner surface 104 andthe outer surface 106 to determine if a persistent layer homogeneity ispresent. However, in embodiments where the glass container is formedfrom a laminated glass in which a glass cladding layer of the laminatedglass forms the interior surface of the glass container, theconcentration of constituent components in the interior region iscompared to the concentration of the same components at a point alongthe midpoint line which evenly bisects the glass cladding layer thatforms the interior surface of the glass container. In the embodimentsdescribed herein, the persistent layer homogeneity in the interiorregion of the glass body is such that an extrema (i.e., the minimum ormaximum) of a layer concentration of each of the constituent componentsof the glass composition in the interior region 120 is greater than orequal to about 80% and less than or equal to about 120% of the sameconstituent component at a midpoint of the glass layer which containsthe interior region 120. The persistent layer homogeneity, as usedherein, refers to the state of the glass container when the glasscontainer is in as-formed condition or following one or more surfacetreatments applied to at least the interior surface of the glasscontainer, such as etching or the like. In other embodiments, thepersistent layer homogeneity in the interior region of the glass body issuch that the extrema of the layer concentration of each of theconstituent components of the glass composition in the interior region120 is greater than or equal to about 90% and less than or equal toabout 110% of the same constituent component at the midpoint of thethickness of the glass layer which contains the interior region 120. Instill other embodiments, the persistent layer homogeneity in theinterior region of the glass body is such that the extrema of the layerconcentration of each of the constituent components of the glasscomposition in the interior region 120 is greater than or equal to about92% and less than or equal to about 108% of the same constituentcomponent at the midpoint of the thickness of the glass of the glasslayer which contains the interior region 120. In some embodiments, thepersistent layer homogeneity is exclusive of constituent components ofthe glass composition which are present in an amount less than about 2mol. %.

The term “as-formed condition,” as used herein, refers to thecomposition of the glass container 100 after the glass container hasbeen formed from glass stock but prior to the container being exposed toany additional processing steps, such as ion-exchange strengthening,coating, ammonium sulfate treatment or the like. In some embodiments,the term “as-formed condition” includes the composition of the glasscontainer 100 after the glass container has been formed and exposed toan etching treatment to selectively remove all or a portion of at leastthe interior surface of the glass container. In the embodimentsdescribed herein, the layer concentration of the constituent componentsin the glass composition is determined by collecting a compositionsample through the thickness of the glass body in the area of interestusing dynamic secondary ion mass spectroscopy (DSIMS). In theembodiments described herein, the composition profile is sampled fromareas of the inner surface 104 of the glass body 102. The sampled areashave a maximum area of 1 mm². This technique yields a compositionalprofile of the species in the glass as a function of depth from theinner surface of the glass body for the sampled area.

Forming the glass container with a persistent layer homogeneity asdescribed above, generally improves the resistance of the glasscontainer to delamination. Specifically, providing an interior regionwhich is homogenous in composition (i.e., the extrema of theconcentration of the constituent components in the interior region iswithin +/−20% of the same constituent components at the midpoint of thethickness of the glass layer which contains the interior region) avoidsthe localized concentration of constituent components of the glasscomposition which may be susceptible to leaching which, in turn,mitigates the loss of glass particles from the inner surface of theglass container in the event that these constituent components areleached from the glass surface.

As noted herein, the container with the persistent layer homogeneity inas-formed condition is free from coatings, including inorganic and/ororganic coatings applied to the inner surface of the glass body.Accordingly, it should be understood that the body of the glasscontainer is formed from a substantially unitary composition whichextends from the inner surface of the body to a depth of at least 250 nmor even at least 300 nm. The term “unitary composition” refers to thefact that the glass from which the portion of the body extending fromthe inner surface into the thickness of the body to a depth of at least250 nm or even at least 300 nm is formed is a single composition ofmaterial as compared to a coating material applied to another materialof either the same or different composition. For example, in someembodiments, the body of the container may be constructed from a singleglass composition. In other embodiments, the body of the container maybe constructed from a laminated glass such that the inner surface of thebody has a unitary composition which extends from the inner surface to adepth of at least 250 nm or even at least 300 nm. The glass containermay include an interior region which extends from either the innersurface or from 10 nm below the inner surface to a depth of at least 100nm, as noted above. This interior region may have a persistent layerhomogeneity.

Referring now to FIGS. 1 and 7, in some embodiments, the glasscontainers described herein may also have a homogenous surfacecomposition over the inner surface 104 of the body 102 such that atleast the inner surface 104 of the body 102, including in the wall,heel, and floor portions, has a delamination factor of 10 or less whenthe glass container is in as-formed condition. FIG. 7 schematicallydepicts a partial cross section of a wall portion 110 of the glasscontainer 100. The glass container 100 has a surface region 130 whichextends over the entire inner surface of the glass container. Thesurface region 130 has a depth D_(SR) which extends from the innersurface 104 of the glass container 100 into a thickness of the glassbody towards the exterior surface. Accordingly, it should be understoodthat the surface region 130 has a thickness T_(SR) which is equal to thedepth D_(SR). In some embodiments, the surface region extends to a depthD_(SR) of at least about 10 nm from the inner surface 104 of the glasscontainer 100. In some other embodiments, the surface region 130 mayextend to a depth D_(SR) of at least about 50 nm. In some otherembodiments, the surface region 130 may extend to a depth D_(SR) fromabout 10 nm to about 50 nm. Accordingly, it should be understood thatthe surface region 130 extends to a shallower depth than the interiorregion 120. The glass composition of the surface region has a persistentsurface homogeneity which, in conjunction with the depth D_(SR) of theinterior region, is sufficient to prevent delamination of the glass bodyfollowing long term exposure to a solution contained in the interiorvolume of the glass container.

In the embodiments described herein, the phrase “persistent surfacehomogeneity” means that the concentration of the constituent components(e.g., SiO₂, Al₂O₃, Na₂O, etc.) of the glass composition at a discretepoint in the surface region do not vary from the concentration of thesame constituent components at any second discrete point in the surfaceregion by an amount which would result in delamination of the glass bodyupon long term exposure to a solution contained within the glasscontainer. In the embodiments described herein, the persistent surfacehomogeneity in the surface region is such that, for a discrete point onthe inner surface 104 of the glass container, the extrema (i.e., theminimum or maximum) of the surface concentration of each of theconstituent components in the surface region 130 at a discrete point isgreater than or equal to about 70% and less than or equal to about 130%of the same constituent components in the surface region 130 at anysecond discrete point on the inner surface 104 of the glass container100 when the glass container 100 is in as-formed condition. For example,FIG. 7 depicts three discrete points (A, B, and C) on the inner surface104 of the wall portion 110. Each point is separated from an adjacentpoint by at least about 3 mm. The extrema of the surface concentrationof each of the constituent components in the surface region 130 at point“A” is greater than or equal to about 70% and less than or equal toabout 130% of the same constituent components in the surface region 130at points “B” and “C”. When referring to the heel portion of thecontainer, the discrete points may be approximately centered at the apexof the heel with adjacent points located at least 3 mm from the apex ofthe heel along the floor portion of the container and along the wallportion of the container, the distance between the points being limitedby the radius of the container and the height of the sidewall (i.e., thepoint where the sidewall transitions to the shoulder of the container).

In some embodiments, the persistent surface homogeneity in the surfaceregion is such that the extrema of the surface concentration of each ofthe constituent components of the glass composition in the surfaceregion 130 for any discrete point on the inner surface 104 of the glasscontainer 100 is greater than or equal to about 75% and less than orequal to about 125% of the same constituent component in the surfaceregion 130 at any second discrete point on the inner surface 104 of theglass container 100. In some other embodiments, the persistent surfacehomogeneity in the surface region is such that the extrema of thesurface concentration of each of the constituent components of the glasscomposition in the surface region 130 for any discrete point on theinner surface 104 of the glass container 100 is greater than or equal toabout 80% and less than or equal to about 120% of the same constituentcomponent in the surface region 130 at any second discrete point on theinner surface 104 of the glass container 100. In still otherembodiments, the persistent surface homogeneity in the surface region issuch that the extrema of the surface concentration of each of theconstituent components of the glass composition in the surface region130 for any discrete point on the inner surface 104 of the glasscontainer 100 is greater than or equal to about 85% and less than orequal to about 115% of the same constituent component in the surfaceregion 130 at any second discrete point on the inner surface 104 of theglass container 100. In the embodiments described herein, the surfaceconcentration of the constituent components of the glass composition inthe surface region is measured by x-ray photoelectron spectroscopy. Insome embodiments, the persistent surface homogeneity in the surfaceregion is exclusive of constituent components of the glass compositionwhich are present in an amount less than about 2 mol. %.

The homogeneity of the surface concentration of the glass constituentcomponents in the surface region 130 is generally an indication of thepropensity of the glass composition to delaminate and shed glassparticles from the inner surface 104 of the glass container 100. Whenthe glass composition has a persistent surface homogeneity in thesurface region 130 (i.e., when the extrema of the surface concentrationof the glass constituent components in the surface region 130 at adiscrete point on the inner surface 104 are within +/−30% of the sameconstituent components in the surface region 130 at any second discretepoint on the inner surface 104), the glass composition has improvedresistance to delamination.

Glass containers having persistent layer homogeneity and/or persistentsurface homogeneity may be achieved using various techniques. Forexample, in some embodiments, at least the inner surface 104 of the body102 of the glass container is etched which produces a glass containerhaving a persistent layer homogeneity and/or a persistent surfacehomogeneity such that at least the inner surface of the glass containerhas a delamination factor of 10 or less. Specifically, compositionalvariations in the glass due to volatilization of species from the glassand subsequent re-deposition of the volatized species during containerformation, as described above, is believed to be one mechanism thatleads to delamination. The thin skin of volatized and re-depositedspecies on the inner surface of the glass container is compositionallyheterogeneous and hydrolytically weak such that alkali and boron speciesare quickly depleted from the skin during exposure to pharmaceuticalcompositions. This behavior leaves behind a silica rich layer with ahigh surface area. Exposure of this silica rich layer to apharmaceutical composition causes the layer to swell and, ultimately,flake off (i.e., delaminate) from the inner surface of the body.However, etching the inner surface of the body of the glass containerremoves this thin skin layer and imparts a persistent layer homogeneityand/or persistent surface homogeneity to at least the inner surface ofthe body of the glass container.

In some embodiments described herein, the body of the glass container isetched to remove a layer of glass material from the inner surface of theglass body. The etch is sufficient to remove the thin skin layer ofvolatized and re-deposited species and thereby provide a persistentlayer homogeneity and/or a persistent surface homogeneity to at leastthe inner surface of the body of the glass container such that at leastthe inner surface of the glass body has a delamination factor of 10 orless. For example, in some embodiments, the body of the glass containeris etched to remove glass material from the inner surface of the glassbody to a depth of 1 μm or even 1.5 μm. In some other embodiments, thebody of the glass container may be etched to remove glass material to adepth greater than 1.5 μm, including, without limitation, 2 μm, 3 μm oreven 5 μm. In these embodiments, at least the interior surface of theglass container may be formed from glass compositions which meet thecriteria for Type I, Class A (Type IA) or Type I, Class B (Type IB)glasses under ASTM Standard E438-92 (2011) entitled “StandardSpecification for Glasses in Laboratory Apparatus”. Borosilicate glassesmeet the Type I (A or B) criteria and are routinely used forpharmaceutical packaging. Examples of borosilicate glass include,without limitation, Corning® Pyrex® 7740, 7800, Wheaton 180, 200, and400, Schott Duran®, Schott Fiolax®, KIMAX® N-51A, Gerresheimer GX-51Flint and others.

In one embodiment, etching may be accomplished by exposing the innersurface of the glass container to an acid solution, or a combination ofacid solutions. The acid solutions may include, without limitation,sulfuric acid, nitric acid, hydrochloric acid, hydrofluoric acid,hydrobromic acid, and phosphoric acid. For example, the acid solutionmay include a mixture of 1.5 M hydrofluoric acid with 0.9 M sulfuricacid. These acid solutions effectively remove the thin skin layer ofvolatized and re-deposited organic solution without leaving a depleted“leach layer” on the inner surface of the glass container.Alternatively, etching may be accomplished by exposing the inner surfaceof the glass container to a base solution or a combination of basesolutions. Suitable base solutions include, for example, sodiumhydroxide, potassium hydroxide, ammonium hydroxide, or combinationsthereof. Alternatively, etching may be accomplished by sequentially acidsolutions followed by base solutions or vice-versa.

While one specific etching treatment is described herein, it should beunderstood that other etching treatments may also be used. For example,the etching treatments disclosed in U.S. Pat. No. 2,106,744, U.S. PatentPublication No. 2011/0165393, U.S. Patent Publication No. 2013/0122306,and U.S. Patent Publication No. 2012/0282449 may also be used to etch atleast the interior surface of the glass container.

In still other embodiments, glass containers may be provided with apersistent layer homogeneity and/or a persistent surface homogeneity byforming the glass containers from glass compositions in which theconstituent components of the glass composition form species withrelatively low vapor pressures (i.e., species with a low volatility) atthe temperatures required to reform the glass containers from glassstock into the desired container shape. Because these constituentcomponents form species with relatively low vapor pressures at thereforming temperatures, the constituent components are less likely tovolatilize and evaporate from the surfaces of the glass, thereby forminga glass container with a compositionally homogenous surface over theinner surface of the glass container and through the thickness of theglass container.

Certain constituent components of the glass composition may besufficiently volatile at the glass forming and reforming temperatureswhich, in turn, may lead to compositional heterogeneities and subsequentdelamination. Forming and reforming temperatures of the glasscomposition generally correspond to the temperatures at which the glasscomposition has a viscosity in the range from about 200 poise to about100 kilopoise. Accordingly, in some embodiments, the glass compositionsfrom which the glass containers are formed are free from constituentcomponents which form species that volatilize significantly (i.e., formgas phase species with equilibrium partial pressures greater than about10⁻³ atm) at temperatures corresponding to a viscosity in the range fromabout 200 poise to about 100 kilopoise. In some embodiments, the glasscompositions from which the glass containers are formed are free fromconstituent components which volatilize significantly at temperaturescorresponding to a viscosity in the range from about 1 kilopoise toabout 50 kilopoise. In some other embodiments, the glass compositionsfrom which the glass containers are formed are free from constituentcomponents which volatilize significantly at temperatures correspondingto a viscosity in the range from about 1 kilopoise to about 20kilopoise. In some other embodiments, the glass compositions from whichthe glass containers are formed are free from constituent componentswhich volatilize significantly at temperatures corresponding to aviscosity in the range from about 1 kilopoise to about 10 kilopoise.Without wishing to be bound by theory, compounds which volatilizesignificantly under these conditions include, without limitation, boronand compounds of boron, phosphorous and compounds of phosphorous, zincand compounds of zinc, fluorine and compounds of fluorine, chlorine andcompounds of chlorine, tin and compounds of tin, and sodium andcompounds of sodium.

In some embodiments described herein, the glass containers are generallyformed from aluminosilicate glass compositions, such as alkalialuminosilicate glass compositions or alkaline-earth aluminosilicateglass compositions, for example. As noted hereinabove, boron containingspecies in the glass are highly volatile at the elevated temperaturesused for glass forming and reforming which leads to delamination of theresultant glass container. Moreover, glass compositions containing boronare also susceptible to phase separation. Accordingly, in theembodiments described herein, the boron concentration in the glasscompositions from which the glass containers are formed is limited tomitigate both delamination and phase separation. In some embodiments,the glass compositions from which the glass containers are formedincludes less than or equal to about 1.0 mol. % of oxides of boronand/or compounds containing boron, including, without limitation, B₂O₃.In some of these embodiments, the concentration of oxides of boronand/or compounds containing boron in the glass composition may be lessthan or equal to about 0.5 mol. %, less than or equal to about 0.4 mol.% or even less than or equal to about 0.3 mol. %. In some of theseembodiments, the concentration of oxides of boron and/or compoundscontaining boron in the glass composition may be less than or equal toabout 0.2 mol. % or even less than or equal to about 0.1 mol. %. In someother embodiments, the glass compositions are substantially free fromboron and compounds containing boron.

Phosphorous, like boron, generally forms species in the glasscomposition which are highly volatile at the elevated temperatures usedfor glass forming and reforming. As such, phosphorous in the glasscomposition can lead to compositional heterogeneities in the finishedglass container which, in turn, may lead to delamination. Accordingly,in the embodiments described herein, the concentration of phosphorousand compounds containing phosphorous (such as P₂O₅ or the like) in theglass compositions from which the glass containers are formed is limitedto mitigate delamination. In some embodiments, the glass compositionsfrom which the glass containers are made includes less than or equal toabout 0.3 mol. % of oxides of phosphorous and/or compounds containingphosphorous. In some of these embodiments, the concentration of oxidesof phosphorous and/or compounds containing phosphorous in the glasscomposition may be less than or equal to about 0.2 mol. % or even lessthan or equal to about 0.1 mol. %. In some other embodiments, the glasscompositions are substantially free from phosphorous and compoundscontaining phosphorous.

Zinc, like boron and phosphorous, generally forms species in the glasscomposition which are highly volatile at the elevated temperatures usedfor glass forming and reforming. As such, zinc in the glass compositioncan lead to compositional heterogeneities in the finished glasscontainer which, in turn, may lead to delamination. Accordingly, in theembodiments described herein, the concentration of zinc and compoundscontaining zinc (such as ZnO or the like) in the glass compositions fromwhich the glass containers are formed is limited to mitigatedelamination. In some embodiments, the glass compositions from which theglass containers are made includes less than or equal to about 0.5 mol.% of oxides of zinc and/or compounds containing zinc. In some otherembodiments, the glass compositions from which the glass containers aremade includes less than or equal to about 0.3 mol. % of oxides of zincand/or compounds containing zinc. In some of these embodiments, theconcentration of oxides of zinc or compounds containing zinc in theglass composition may be less than or equal to about 0.2 mol. % or evenless than or equal to about 0.1 mol. %. In some other embodiments, theglass compositions are substantially free from zinc and compoundscontaining zinc.

Lead and bismuth also form species in the glass composition which arehighly volatile at the elevated temperatures used for glass forming andreforming. Accordingly, in the embodiments described herein, theconcentration of lead, bismuth, compounds containing lead, and compoundscontaining bismuth in the glass compositions from which the glasscontainers are formed is limited to mitigate delamination. In someembodiments, oxides of lead, oxides of bismuth, compounds containinglead and/or compounds containing bismuth, are each present in the glasscompositions in concentrations of less than or equal to about 0.3 mol.%. In some of these embodiments, oxides of lead, oxides of bismuth,compounds containing lead and/or, compounds containing bismuth are eachpresent in the glass compositions in concentrations of less than orequal to about 0.2 mol. % or even concentrations of less than about 0.1mol. %. In some other embodiments, the glass compositions aresubstantially free from lead and/or bismuth and compounds containinglead and/or bismuth.

Species containing chlorine, fluorine, and oxides of tin, are alsohighly volatile at the elevated temperatures used for glass forming andreforming. Accordingly, in the embodiments described herein, chlorine,fluorine, and oxides of tin and compounds containing tin, chlorine, orfluorine, are present in the glass compositions in concentrations whichdo not affect the resistance to delamination of the resultant glass.Specifically, chlorine, fluorine, and oxides of tin and compoundscontaining tin, chlorine, or fluorine, are present in the glasscompositions from which the glass containers are formed inconcentrations less than or equal to about 0.5 mol. % or even less thanor equal to about 0.3 mol. %. In some embodiments, the glasscompositions are substantially free from tin, chlorine, and fluorine,and compounds containing tin, chlorine, or fluorine.

While some embodiments of the glass container may be free from readilyvolatized constituent components as described above, in certain otherembodiments the glass containers may be formed from glass compositionswhich include these volatile constituents, such as when the glasscontainer includes a barrier layer.

The glass compositions from which the containers are formed are notphase separated. The term “phase separated,” as used herein, refers tothe separation of the glass composition into separate phases with eachphase having different compositional characteristics. For example,alkali borosilicate glasses are generally known to phase separate atelevated temperatures (such as the forming and reforming temperatures)into a boron-rich phase and a silica-rich phase. In some embodimentsdescribed herein, the concentration of oxides of boron in the glasscompositions is sufficiently low (i.e., less than or equal to about 1.0mol. %) such that the glass compositions do not undergo phaseseparation.

In one exemplary embodiment, the glass containers are formed from adelamination resistant glass composition such as the alkaline earthaluminosilicate glass compositions described in U.S. patent applicationSer. No. 13/660,141 filed Oct. 25, 2012 and entitled “Alkaline EarthAlumino-Silicate Glass Compositions with Improved Chemical andMechanical Durability” (Attorney Docket No. SP11-241), the entirety ofwhich is incorporated herein by reference. This first exemplary glasscomposition generally includes a combination of SiO₂, Al₂O₃, at leastone alkaline earth oxide, and alkali oxide including at least Na₂O andK₂O. In some embodiments, the glass compositions may also be free fromboron and compounds containing boron. The combination of thesecomponents enables a glass composition which is resistant to chemicaldegradation and is also suitable for chemical strengthening by ionexchange. In some embodiments, the glass compositions may furthercomprise minor amounts of one or more additional oxides such as, forexample, SnO₂, ZrO₂, ZnO, or the like. These components may be added asfining agents and/or to further enhance the chemical durability of theglass composition.

In the embodiments of the first exemplary glass composition, the glasscomposition generally comprises SiO₂ in an amount greater than or equalto about 65 mol. % and less than or equal to about 75 mol. %. In someembodiments SiO₂ is present in the glass composition in an amountgreater than or equal to about 67 mol. % and less than or equal to about75 mol. %. In some other embodiments, SiO₂ is present in the glasscomposition in an amount greater than or equal to about 67 mol. % andless than or equal to about 73 mol. %. In each of these embodiments, theamount of SiO₂ present in the glass composition may be greater than orequal to about 70 mol. % or even greater than or equal to about 72 mol.%.

The first exemplary glass composition also includes Al₂O₃. Al₂O₃, inconjunction with alkali oxides present in the glass compositions such asNa₂O or the like, improves the susceptibility of the glass to ionexchange strengthening. Moreover, additions of Al₂O₃ to the compositionreduce the propensity of alkali constituents (such as Na and K) fromleaching out of the glass and, as such, additions of Al₂O₃ increase theresistance of the composition to hydrolytic degradation. Moreover,additions of Al₂O₃ greater than about 12.5 mol. % may also increase thesoftening point of the glass thereby reducing the formability of theglass. Accordingly, the glass compositions described herein generallyinclude Al₂O₃ in an amount greater than or equal to about 6 mol. % andless than or equal to about 12.5 mol. %. In some embodiments, the amountof Al₂O₃ in the glass composition is greater than or equal to about 6mol. % and less than or equal to about 10 mol. %. In some otherembodiments, the amount of Al₂O₃ in the glass composition is greaterthan or equal to about 7 mol. % and less than or equal to about 10 mol.%.

The first exemplary glass composition also includes at least two alkalioxides. The alkali oxides facilitate the ion exchangeability of theglass composition and, as such, facilitate chemically strengthening theglass. The alkali oxides also lower the softening point of the glass,thereby offsetting the increase in the softening point due to higherconcentrations of SiO₂ in the glass composition. The alkali oxides alsoassist in improving the chemical durability of the glass composition.The alkali oxides are generally present in the glass composition in anamount greater than or equal to about 5 mol. % and less than or equal toabout 12 mol. %. In some of these embodiments, the amount of alkalioxides may be greater than or equal to about 5 mol. % and less than orequal to about 10 mol. %. In some other embodiments, the amount ofalkali oxide may be greater than or equal to about 5 mol. % and lessthan or equal to about 8 mol. %. In all the glass compositions describedherein, the alkali oxides comprise at least Na₂O and K₂O. In someembodiments, the alkali oxides further comprise Li₂O.

The ion exchangeability of the glass composition is primarily impartedto the glass composition by the amount of the alkali oxide Na₂Oinitially present in the glass composition prior to ion exchange.Specifically, in order to achieve the desired compressive stress anddepth of layer in the glass composition upon ion exchange strengthening,the glass compositions include Na₂O in an amount greater than or equalto about 2.5 mol. % and less than or equal to about 10 mol. % based onthe molecular weight of the glass composition. In some embodiments, theglass composition may include Na₂O in an amount greater than or equal toabout 3.5 mol. % and less than or equal to about 8 mol. %. In some ofthese embodiments, the glass composition may include Na₂O in an amountgreater than or equal to about 6 mol. % and less than or equal to about8 mol. %.

As noted above, the alkali oxides in the glass composition also includeK₂O. The amount of K₂O present in the glass composition also relates tothe ion exchangeability of the glass composition. Specifically, as theamount of K₂O present in the glass composition increases, thecompressive stress obtainable through ion exchange decreases.Accordingly, it is desirable to limit the amount of K₂O present in theglass composition. In some embodiments, the amount of K₂O is greaterthan 0 mol. % and less than or equal to about 2.5 mol. % by molecularweight of the glass composition. In some of these embodiments, theamount of K₂O present in the glass composition is less than or equal toabout 0.5 mol. % by molecular weight of the glass composition.

In some embodiments, the alkali oxide in the first exemplary glasscomposition further comprises Li₂O. Including Li₂O in the glasscomposition further decreases the softening point of the glass. Inembodiments where the alkali oxide includes Li₂O, the Li₂O may bepresent in an amount greater than or equal to about 1 mol. % and lessthan or equal to about 3 mol. %. In some embodiments, Li₂O may bepresent in the glass composition in an amount which is greater thanabout 2 mol. % and less than or equal to about 3 mol. %. However, insome other embodiments, the glass composition may be substantially freeof lithium and compounds containing lithium.

Alkaline earth oxides in the first exemplary glass composition improvethe meltability of the glass batch materials and increase the chemicaldurability of the glass composition. The presence of alkaline earthoxides in the glass composition also reduces the susceptibility of theglass to delamination. In the glass compositions described herein, theglass compositions generally include at least one alkaline earth oxidein a concentration greater than or equal to about 8 mol. % or even 8.5mol. % and less than or equal to about 15 mol. %. In some embodiments,the glass composition may comprise from about 9 mol. % to about 15 mol.% of alkaline earth oxide. In some of these embodiments, the amount ofalkaline earth oxide in the glass composition may be from about 10 mol.% to about 14 mol. %.

The alkaline earth oxide in the first exemplary glass composition mayinclude MgO, CaO, SrO, BaO or combinations thereof. For example, in theembodiments described herein the alkaline earth oxide may include MgO.In some embodiments, MgO may be present in the glass composition in anamount which is greater than or equal to about 2 mol. % and less than orequal to about 7 mol. % by molecular weight of the glass composition, oreven greater than or equal to about 3 mol. % and less than or equal toabout 5 mol. % by molecular weight of the glass composition.

In some embodiments, the alkaline earth oxide in the first exemplaryglass composition also includes CaO. In these embodiments, CaO ispresent in the glass composition in an amount from about 2 mol. % toless than or equal to 7 mol. % by molecular weight of the glasscomposition. In some embodiments, CaO is present in the glasscomposition in an amount from about 3 mol. % to less than or equal to 7mol. % by molecular weight of the glass composition. In some of theseembodiments, CaO may be present in the glass composition in an amountgreater than or equal to about 4 mol. % and less than or equal to about7 mol. %. In some other embodiments, CaO may be present in the glasscomposition in an amount greater than or equal to about 5 mol. % andless than or equal to about 6 mol. %, such as when CaO is substitutedfor MgO in the alkaline earth oxide to decrease the liquidus temperatureand increase the liquidus viscosity. In still other embodiments, CaO maybe present in the glass in an amount greater than or equal to about 2mol. % and less than or equal to about 5 mol. %, such as when SrO issubstituted for MgO in the alkaline earth oxide to decrease the liquidustemperature and increase the liquidus viscosity.

In some embodiments described herein, the alkaline earth oxide furthercomprises at least one of SrO or BaO. The inclusion of SrO reduces theliquidus temperature of the glass composition and, as a result, improvesthe formability of the glass composition. In some embodiments the glasscomposition may include SrO in an amount greater than 0 mol. % and lessthan or equal to about 6.0 mol. %. In some other embodiments, the glasscomposition may include SrO in an amount greater than about 0 mol. % andless than or equal to about 5 mol. %. In some of these embodiments, theglass composition may include greater than or equal to about 2 mol. %and less than or equal to about 4 mol. % SrO, such as when CaO issubstituted for MgO in the alkaline earth oxide to decrease the liquidustemperature and increase the liquidus viscosity. In some otherembodiments, the glass composition may include from about 1 mol. % toabout 2 mol. % SrO. In still other embodiments, SrO may be present inthe glass composition in an amount greater than or equal to about 3 mol.% and less than or equal to about 6 mol. %, such as when SrO issubstituted for MgO in the alkaline earth oxide to decrease the liquidustemperature and increase the liquidus viscosity.

In embodiments where the glass composition includes BaO, the BaO may bepresent in an amount greater than about 0 mol. % and less than about 2mol. %. In some of these embodiments, BaO may be present in the glasscomposition in an amount less than or equal to about 1.5 mol. % or evenless than or equal to about 0.5 mol. %. However, in some otherembodiments, the glass composition is substantially free from barium andcompounds of barium.

In the embodiments of the glass compositions described herein, the glasscompositions generally contain less than about 1 mol. % of boron oroxides of boron, such as B₂O₃. For example, in some embodiments theglass compositions may comprise greater than or equal to about 0 mol. %B₂O₃ and less than or equal to 1 mol. % B₂O₃. In some other embodiments,the glass compositions may comprise greater than or equal to about 0mol. % B₂O₃ and less than or equal to 0.6 mol. % B₂O₃. In still otherembodiments, the glass compositions are substantially free from boronand compounds of boron such as B₂O₃. Specifically, it has beendetermined that forming the glass composition with a relatively lowamount of boron or compounds of boron (i.e., less than or equal to 1mol. %) or without boron or compounds of boron significantly increasesthe chemical durability of the glass composition. In addition, it hasalso been determined that forming the glass composition with arelatively low amount of boron or compounds of boron or without boron orcompounds of boron improves the ion exchangeability of the glasscompositions by reducing the process time and/or temperature required toachieve a specific value of compressive stress and/or depth of layer.

In some embodiments of the glass compositions described herein, theglass compositions are substantially free from phosphorous and compoundscontaining phosphorous including, without limitation, P₂O₅.Specifically, it has been determined that formulating the glasscomposition without phosphorous or compounds of phosphorous increasesthe chemical durability of the glass composition.

In addition to the SiO₂, Al₂O₃, alkali oxides and alkaline earth oxides,the first exemplary glass compositions described herein may optionallyfurther comprise one or more fining agents such as, for example, SnO₂,As₂O₃, and/or Cl⁻ (from NaCl or the like). When a fining agent ispresent in the glass composition, the fining agent may be present in anamount less than or equal to about 1 mol. % or even less than or equalto about 0.5 mol. %. For example, in some embodiments the glasscomposition may include SnO₂ as a fining agent. In these embodimentsSnO₂ may be present in the glass composition in an amount greater thanabout 0 mol. % and less than or equal to about 0.30 mol. %.

Moreover, the glass compositions described herein may comprise one ormore additional metal oxides to further improve the chemical durabilityof the glass composition. For example, the glass composition may furtherinclude ZnO or ZrO₂, each of which further improves the resistance ofthe glass composition to chemical attack. In these embodiments, theadditional metal oxide may be present in an amount which is greater thanor equal to about 0 mol. % and less than or equal to about 2.0 mol. %.For example, when the additional metal oxide is ZrO₂, the ZrO₂ may bepresent in an amount less than or equal to about 1.5 mol. %.Alternatively or additionally, the additional metal oxide may includeZnO in an amount less than or equal to about 2.0 mol. %. In someembodiments, ZnO may be included as a substitute for one or more of thealkaline earth oxides. For example, in embodiments where the glasscomposition includes the alkaline earth oxides MgO, CaO and SrO, theamount of MgO may be reduced to decrease the liquidus temperature andincrease the liquidus viscosity, as described above. In theseembodiments, ZnO may be added to the glass composition as a partialsubstitute for MgO, in addition to or in place of at least one of CaO orSrO.

Based on the foregoing, it should be understood that, in one embodiment,the first exemplary glass composition may include from about 65 mol. %to about 75 mol. % SiO₂; from about 6 mol. % to about 12.5 mol. % Al₂O₃;and from about 5 mol. % to about 12 mol. % alkali oxide, wherein thealkali oxide comprises Na₂O and K₂O. The K₂O may be present in an amountless than or equal to 0.5 mol. %. The glass composition may also includefrom about 8.0 mol. % to about 15 mol. % of alkaline earth oxide. Theglass composition may be susceptible to strengthening by ion-exchange.

In another embodiment of the first exemplary glass composition, theglass composition includes from about 67 mol. % to about 75 mol. % SiO₂;from about 6 mol. % to about 10 mol. % Al₂O₃; from about 5 mol. % toabout 12 mol. % alkali oxide; and from about 9 mol. % to about 15 mol. %of alkaline earth oxide. The alkali oxide comprises at least Na₂O andK₂O. The glass composition is free from boron and compounds of boron andis susceptible to ion exchange thereby facilitating chemicallystrengthening the glass to improve the mechanical durability.

In yet another embodiment of the first exemplary glass composition, theglass composition may include from about 67 mol. % to about 75 mol. %SiO₂; from about 6 mol. % to about 10 mol. % Al₂O₃; from about 5 mol. %to about 12 mol. % alkali oxide; and from about 9 mol. % to about 15mol. % of alkaline earth oxide. The alkaline earth oxide comprises atleast one of SrO and BaO. The glass composition is free from boron andcompounds of boron and is susceptible to ion exchange therebyfacilitating chemically strengthening the glass to improve themechanical durability.

In some embodiments described herein, glass containers with persistentsurface homogeneity and/or persistent layer homogeneity may be obtainedutilizing forming processes which impart a uniform temperature historyto at least the inner surface of the body of the glass container. Forexample, in one embodiment, the body of the glass container may beformed at forming temperatures and/or forming speeds which mitigate thevolatilization of chemical species from the glass composition from whichthe body is formed. Specifically, forming a glass stream into a desiredshape requires control of both the viscosity of the glass and the speedof formation. Higher viscosities require slower forming speeds, whilelower viscosities enable faster forming speeds. The bulk composition ofthe glass and the temperature are the largest drivers for affectingviscosity. It is possible to use the same forming process for differentglasses by matching viscosities at each stage in the forming process byadjusting temperature. Accordingly, one approach to reducingvolatilization from a glass melt is to operate the process at a lowertemperature (higher viscosity). This approach is disadvantageous becauseit also requires slowing the yield and capacity of the formingequipment, ultimately leading to increased cost. FIG. 16 shows thattemperature is a large driver for volatilization in two exemplarycompositions, and that in all cases reducing temperature (and thereforespeed) reduces the driving force for volatilization loss. The viscosityassociated with tube-to-vial conversion processes range from 200P(highest temperature, at cutting and hole-punch operations) to 20,000P(lowest temperature, at tube forming and finishing steps). For typical51-expansion borosilicates, these viscosities are approximately1100-1650° C. Since volatilization is reduced significantly at the lowertemperatures, the primary temperature range of concern is between1350-1650° C.

In another embodiment glass containers with persistent surfacehomogeneity and/or persistent layer homogeneity may be obtained bymold-forming the body. There are several methods for forming a glassmelt into a container shape using molds. All rely on introduction of auniformly hot ‘gob’ of molten glass to a forming machine. Inblow-and-blow molding, the gob is first blown using pressurized airthrough an orifice (which shapes the lip/finish) to create a preform(smaller than the end product). The preform (or parison) is then placedinto a second mold where it is further blown into contact with the moldsurface and defines the final shape of the container. In press-and-blowmolding, the gob is held by a ring which defines the lip/finish and aplunger is pressed through the gob to form the preform. The preform isthen placed in the second mold and blown into contact with the moldsurface, forming the final container shape. The mold forming processgenerally imparts a uniform temperature history to the body duringforming which, in turn, may impart a persistent surface homogeneityand/or a persistent layer homogeneity to at least the inner surface ofthe glass body, thereby decreasing the susceptibility of the glass bodyto delamination. For example, the molten glass may be formed into thecontainer shape and the temperature of the glass controlled duringcooling such that the glass body is monotonically cooled from the glassmelt. Monotonic cooling occurs when the temperature of the glass body isdecreased from the melt to solidification without any intermediateincreases in temperature. This results in less volatilization relativeto processes which convert tubes into vials. This type of cooling may befacilitated using mold-forming processes such as blow molding,press-and-blow molding, blow-blow molding. In some embodiments, thesetechniques may be used to form a glass container with a delaminationfactor of 10 or less from Type I Class B glass compositions.

The glass compositions described herein are formed by mixing a batch ofglass raw materials (e.g., powders of SiO₂, Al₂O₃, alkali oxides,alkaline earth oxides and the like) such that the batch of glass rawmaterials has the desired composition. Thereafter, the batch of glassraw materials is heated to form a molten glass composition which issubsequently cooled and solidified to form the glass composition. Duringsolidification (i.e., when the glass composition is plasticallydeformable) the glass composition may be shaped using standard formingtechniques to shape the glass composition into a desired final form.Alternatively, the glass composition may be shaped into a stock form,such as a sheet, tube or the like, and subsequently reheated and formedinto the glass container 100.

The glass compositions described herein may be shaped into various formssuch as, for example, sheets, tubes or the like. Chemically durableglass compositions are particularly well suited for use in the formationof pharmaceutical packages for containing a pharmaceutical formulation,such as liquids, powders and the like. For example, the glasscompositions described herein may be used to form glass containers suchas vials, ampoules, cartridges, syringe bodies and/or any other glasscontainer for storing pharmaceutical formulations. Moreover, the abilityto chemically strengthen the glass compositions through ion exchange canbe utilized to improve the mechanical durability of such pharmaceuticalpackaging. Accordingly, it should be understood that, in at least oneembodiment, the glass compositions are incorporated in a pharmaceuticalpackage in order to improve the chemical durability and/or themechanical durability of the pharmaceutical packaging.

Further, in some embodiments, the glass containers may be formed fromglass compositions that are chemically durable and resistant todegradation as determined by the DIN 12116 standard, the ISO 695standard, the ISO 719 standard, the ISO 720 standard, the USP <660> testand/or the European Pharmacopeia 3.2.1 test.

Specifically, the DIN 12116 standard is a measure of the resistance ofthe glass to decomposition when placed in an acidic solution. The DIN12116 standard is broken into individual classes. Class S1 indicatesweight losses of up to 0.7 mg/dm²; Class S2 indicates weight losses from0.7 mg/dm² up to 1.5 mg/dm²; Class S3 indicates weight losses from 1.5mg/dm² up to 15 mg/dm²; and Class S4 indicates weight losses of morethan 15 mg/dm². The glass compositions described herein have an acidresistance of class S3 or better according to DIN 12116 with someembodiments having an acid resistance of at least class S2 or better oreven class 51. It should be understood that lower class rankings haveimproved acid resistance performance. Accordingly, a composition gradedat 51 has better acid resistance than a composition graded at class S2.

The ISO 695 standard is a measure of the resistance of the glass todecomposition when placed in a basic solution. The ISO 695 standard isbroken into individual classes. Class A1 indicates weight losses of upto 75 mg/dm²; Class A2 indicates weight losses from 75 mg/dm² up to 175mg/dm²; and Class A3 indicates weight losses of more than 175 mg/dm².The glass compositions described herein have a base resistance accordingto ISO 695 of class A2 or better with some embodiments having a class A1base resistance. Is should be understood that lower class rankings haveimproved base resistance performance. Accordingly, a composition gradedat A1 has better base resistance than a composition graded at class A2.

The glass compositions from which the glass containers are formed arechemically durable and resistant to degradation as determined by the ISO720 standard. The ISO 720 standard is a measure of the resistance of theglass to degradation in distilled water (i.e., the hydrolytic resistanceof the glass). Non-ion exchanged samples of glass are assessed accordingto the ISO 720 protocol. Ion exchanged samples of glass are assessedwith a modified ISO 720 protocol in which the glass is crushed to thegrain size required in the ISO 720 standard, ion exchanged in a moltensalt bath of 100% KNO₃ at a temperature of 450° C. for at least 5 hoursto induce a compressive stress layer in the individual grains of glass,and then tested according to the ISO 720 standard. The ISO 720 standardis broken into individual types. Type HGA1 is indicative of up to 62 μgextracted equivalent of Na₂O; Type HGA2 is indicative of more than 62 μgand up to 527 μg extracted equivalent of Na₂O; and Type HGA3 isindicative of more than 527 μg and up to 930 μg extracted equivalent ofNa₂O. The glass compositions described herein have an ISO 720 hydrolyticresistance of type HGA2 or better with some embodiments having a typeHGA1 hydrolytic resistance or better. Is should be understood that lowerclass rankings have improved hydrolytic resistance performance.Accordingly, a composition graded at HGA1 has better hydrolyticresistance than a composition graded at HGA2.

The glass compositions from which the glass containers are formed arealso chemically durable and resistant to degradation as determined bythe ISO 719 standard. The ISO 719 standard is a measure of theresistance of the glass to degradation in distilled water (i.e., thehydrolytic resistance of the glass). Non-ion exchanged samples of glassare assessed according to the ISO 719 protocol. Ion exchanged samples ofglass are assessed with a modified ISO 719 protocol in which the glassis crushed to the grain size required in the ISO 719 standard, ionexchanged in a molten salt bath of 100% KNO₃ at a temperature of 450° C.for at least 5 hours to induce a compressive stress layer in theindividual grains of glass, and then tested according to the ISO 719standard. The ISO 719 standard is broken into individual types. TypeHGB1 is indicative of up to 31 μg extracted equivalent of Na₂O; TypeHGB2 is indicative of more than 31 μg and up to 62 μg extractedequivalent of Na₂O; Type HGB3 is indicative of more than 62 μg and up to264 μg extracted equivalent of Na₂O; Type HGB4 is indicative of morethan 264 μg and up to 620 μg extracted equivalent of Na₂O; and Type HGB5is indicative of more than 620 μg and up to 1085 μg extracted equivalentof Na₂O. The glass compositions described herein have an ISO 719hydrolytic resistance of type HGB2 or better with some embodimentshaving a type HGB1 hydrolytic resistance. Is should be understood thatlower class rankings have improved hydrolytic resistance performance.Accordingly, a composition graded at HGB1 has better hydrolyticresistance than a composition graded at HGB2.

With respect to the USP <660> test and/or the European Pharmacopeia3.2.1 test, the glass containers described herein have a Type 1 chemicaldurability. As noted above, the USP <660> and European Pharmacopeia3.2.1 tests are performed on intact glass containers rather than crushedgrains of glass and, as such, the USP <660> and European Pharmacopeia3.2.1 tests may be used to directly assess the chemical durability ofthe inner surface of the glass containers.

It should be understood that, when referring to the above referencedclassifications according to ISO 719, ISO 720, ISO 695, and DIN 12116, aglass composition or glass article which has a specified classification“or better” means that the performance of the glass composition is asgood as or better than the specified classification. For example, aglass article which has an ISO 719 hydrolytic resistance of “HGB2” orbetter may have an ISO 719 classification of either HGB2 or HGB1.

Damage Resistance

As noted herein above, glass containers may be subject to damage, suchas impact damage, scratches and/or abrasions, as the containers areprocessed and filled. Such damage is often caused by contact betweenindividual glass containers or contact between the glass containers andmanufacturing equipment. This damage generally decreases the mechanicalstrength of the container and may lead to through-cracks which cancompromise the integrity of the contents of the container. Accordingly,in some embodiments described herein, the glass containers 100 furtherinclude a lubricous coating 160 positioned around at least a portion ofthe outer surface 106 of the body 102, as shown in FIG. 8. In someembodiments, the lubricous coating 160 may be positioned on at least theouter surface 106 of the body 102 of the glass container while, in otherembodiments, one or more intermediate coatings may be positioned betweenthe lubricous coating and the outer surface 106 of the body 102, such aswhen an inorganic coating is utilized to compressively stress thesurface of the body 102. The lubricous coating decreases the coefficientof friction of the portion of the body 102 with the coating and, assuch, decreases the occurrence of abrasions and surface damage on theouter surface 106 of the glass body 102. In essence, the coating allowsthe container to “slip” relative to another object (or container)thereby reducing the possibility of surface damage on the glass.Moreover, the lubricous coating 160 also cushions the body 102 of theglass container 100, thereby lessening the effect of blunt impact damageto the glass container.

The term lubricous, as used herein, means that the coating applied tothe outer surface of the glass container has a lower coefficient offriction than the uncoated glass container thereby providing the glasscontainer with an improved resistance to damage such as scuffs,abrasions or the like.

Various properties of the coated glass containers (i.e., coefficient offriction, horizontal compression strength, 4-point bend strength,transparency, colorlessness and the like) may be measured when thecoated glass containers are in an as-coated condition (i.e., followingapplication of the coating without any additional treatments) orfollowing one or more processing treatments, such as those similar oridentical to treatments performed on a pharmaceutical filling line,including, without limitation, washing, lyophilization, depyrogenation,autoclaving, or the like.

Depyrogenation is a process wherein pyrogens are removed from asubstance. Depyrogenation of glass articles, such as pharmaceuticalpackages, can be performed by a thermal treatment applied to a sample inwhich the sample is heated to an elevated temperature for a period oftime. For example, depyrogenation may include heating a glass containerto a temperature of between about 250° C. and about 380° C. for a timeperiod from about 30 seconds to about 72 hours, including, withoutlimitation, 20 minutes, 30 minutes 40 minutes, 1 hour, 2 hours, 4 hours,8 hours, 12 hours, 24 hours, 48 hours, and 72 hours. Following thethermal treatment, the glass container is cooled to room temperature.One conventional depyrogenation condition commonly employed in thepharmaceutical industry is thermal treatment at a temperature of about250° C. for about 30 minutes. However, it is contemplated that the timeof thermal treatment may be reduced if higher temperatures are utilized.The coated glass containers, as described herein, may be exposed toelevated temperatures for a period of time. The elevated temperaturesand time periods of heating described herein may or may not besufficient to depyrogenate a glass container. However, it should beunderstood that some of the temperatures and times of heating describedherein are sufficient to dehydrogenate a coated glass container, such asthe coated glass containers described herein. For example, as describedherein, the coated glass containers may be exposed to temperatures ofabout 250° C., about 260° C., about 270° C., about 280° C., about 290°C., about 300° C., about 310° C., about 320° C., about 330° C., about340° C., about 350° C., about 360° C., about 370° C., about 380° C.,about 390° C., or about 400° C., for a period of time of 30 minutes.

As used herein, lyophilization conditions (i.e., freeze drying) refer toa process in which a sample is filled with a liquid that containsprotein and then frozen at −100° C., followed by water sublimation for20 hours at −15° C. under vacuum.

As used herein, autoclave conditions refer to steam purging a sample for10 minutes at 100° C., followed by a 20 minute dwelling period whereinthe sample is exposed to a 121° C. environment, followed by 30 minutesof heat treatment at 121° C.

The coefficient of friction (μ) of the portion of the coated glasscontainer with the lubricous coating may have a lower coefficient offriction than a surface of an uncoated glass container formed from asame glass composition. A coefficient of friction (μ) is a quantitativemeasurement of the friction between two surfaces and is a function ofthe mechanical and chemical properties of the first and second surfaces,including surface roughness, as well as environmental conditions suchas, but not limited to, temperature and humidity. As used herein, acoefficient of friction measurement for a coated glass container 100 isreported as the coefficient of friction between the outer surface of afirst glass container (having an outer diameter of between about 16.00mm and about 17.00 mm) and the outer surface of second glass containerwhich is identical to the first glass container, wherein the first andsecond glass containers have the same body and the same coatingcomposition (when applied) and have been exposed to the sameenvironments prior to fabrication, during fabrication, and afterfabrication. Unless otherwise denoted herein, the coefficient offriction refers to the maximum coefficient of friction measured with anormal load of 30 N measured on a vial-on-vial testing jig, as describedherein. However, it should be understood that a coated glass containerwhich exhibits a maximum coefficient of friction at a specific appliedload will also exhibit the same or better (i.e., lower) maximumcoefficient of friction at a lesser load. For example, if a coated glasscontainer exhibits a maximum coefficient of friction of 0.5 or lowerunder an applied load of 50 N, the coated glass container will alsoexhibit a maximum coefficient of friction of 0.5 or lower under anapplied load of 25 N.

In the embodiments described herein, the coefficient of friction of theglass containers (both coated and uncoated) is measured with avial-on-vial testing jig. The testing jig 300 is schematically depictedin FIG. 9. The same apparatus may also be used to measure the frictiveforce between two glass containers positioned in the jig. Thevial-on-vial testing jig 300 comprises a first clamp 312 and a secondclamp 322 arranged in a cross configuration. The first clamp 312comprises a first securing arm 314 attached to a first base 316. Thefirst securing arm 314 attaches to the first glass container 310 andholds the first glass container 310 stationary relative to the firstclamp 312. Similarly, the second clamp 322 comprises a second securingarm 324 attached to a second base 326. The second securing arm 324attaches to the second glass container 320 and holds it stationaryrelative to the second clamp 322. The first glass container 310 ispositioned on the first clamp 312 and the second glass container 320 ispositioned of the second clamp 322 such that the long axis of the firstglass container 310 and the long axis of the second glass container 320are positioned at about a 90° angle relative to one another and on ahorizontal plane defined by the x-y axis.

A first glass container 310 is positioned in contact with the secondglass container 320 at a contact point 330. A normal force is applied ina direction orthogonal to the horizontal plane defined by the x-y axis.The normal force may be applied by a static weight or other forceapplied to the second clamp 322 upon a stationary first clamp 312. Forexample, a weight may be positioned on the second base 326 and the firstbase 316 may be placed on a stable surface, thus inducing a measurableforce between the first glass container 310 and the second glasscontainer 320 at the contact point 330. Alternatively, the force may beapplied with a mechanical apparatus, such as a UMT (universal mechanicaltester) machine.

The first clamp 312 or second clamp 322 may be moved relative to theother in a direction which is at a 45° angle with the long axis of thefirst glass container 310 and the second glass container 320. Forexample, the first clamp 312 may be held stationary and the second clamp322 may be moved such that the second glass container 320 moves acrossthe first glass container 310 in the direction of the x-axis. A similarsetup is described by R. L. De Rosa et al., in “Scratch ResistantPolyimide Coatings for Alumino Silicate Glass surfaces” in The Journalof Adhesion, 78: 113-127, 2002. To measure the coefficient of friction,the force required to move the second clamp 322 and the normal forceapplied to first and second glass containers 310, 320 are measured withload cells and the coefficient of friction is calculated as the quotientof the frictive force and the normal force. The jig is operated in anenvironment of 25° C. and 50% relative humidity.

In the embodiments described herein, the portion of the coated glasscontainer with the lubricous coating has a coefficient of friction ofless than or equal to about 0.7 relative to a like-coated glasscontainer, as determined with the vial-on-vial jig described above. Inother embodiments, the coefficient of friction may be less than or equalto about 0.6, or even less than or equal to about 0.5. In someembodiments, the portion of the coated glass container with thelubricous coating has a coefficient of friction of less than or equal toabout 0.4 or even less than or equal to about 0.3. Coated glasscontainers with coefficients of friction less than or equal to about 0.7generally exhibit improved resistance to frictive damage and, as aresult, have improved mechanical properties. For example, conventionalglass containers (without a lubricous coating) may have a coefficient offriction of greater than 0.7.

In some embodiments described herein, the coefficient of friction of theportion of the coated glass container with the lubricous coating is atleast 20% less than a coefficient of friction of a surface of anuncoated glass container formed from a same glass composition. Forexample, the coefficient of friction of the portion of the coated glasscontainer with the lubricous coating may be at least 20% less, at least25% less, at least 30% less, at least 40% less, or even at least 50%less than a coefficient of friction of a surface of an uncoated glasscontainer formed from a same glass composition.

In some embodiments, the portion of the coated glass container with thelubricous coating may have a coefficient of friction of less than orequal to about 0.7 after exposure to a temperature of about 250° C.,about 260° C., about 270° C., about 280° C., about 290° C., about 300°C., about 310° C., about 320° C., about 330° C., about 340° C., about350° C., about 360° C., about 370° C., about 380° C., about 390° C., orabout 400° C., for a period of time of 30 minutes (i.e., depyrogenationconditions). In other embodiments, the portion of the coated glasscontainer with the lubricous coating may have a coefficient of frictionof less than or equal to about 0.7, (i.e., less than or equal to about0.6, less than or equal to about 0.5, less than or equal to about 0.4,or even less than or equal to about 0.3) after exposure to a temperatureof about 250° C., about 260° C., about 270° C., about 280° C., about290° C., about 300° C., about 310° C., about 320° C., about 330° C.,about 340° C., about 350° C., about 360° C., about 370° C., about 380°C., about 390° C., or about 400° C., for a period of time of 30 minutes.In some embodiments, the coefficient of friction of the portion of thecoated glass container with the lubricous coating may not increase bymore than about 30% after exposure to a temperature of about 260° C. for30 minutes. In other embodiments, coefficient of friction of the portionof the coated glass container with the lubricous coating may notincrease by more than about 30% (i.e., about 25%, about 20%, about 15%,or event about 10%) after exposure to a temperature of about 250° C.,about 260° C., about 270° C., about 280° C., about 290° C., about 300°C., about 310° C., about 320° C., about 330° C., about 340° C., about350° C., about 360° C., about 370° C., about 380° C., about 390° C., orabout 400° C., for a period of time of 30 minutes. In other embodiments,coefficient of friction of the portion of the coated glass containerwith the lubricous coating may not increase by more than about 0.5(i.e., about 0.45, about 0.04, about 0.35, about 0.3, about 0.25, about0.2, about 0.15, about 0.1, or event about 0.5) after exposure to atemperature of about 250° C., about 260° C., about 270° C., about 280°C., about 290° C., about 300° C., about 310° C., about 320° C., about330° C., about 340° C., about 350° C., about 360° C., about 370° C.,about 380° C., about 390° C., or about 400° C., for a period of time of30 minutes. In some embodiments, the coefficient of friction of theportion of the coated glass container with the lubricous coating may notincrease at all after exposure to a temperature of about 250° C., about260° C., about 270° C., about 280° C., about 290° C., about 300° C.,about 310° C., about 320° C., about 330° C., about 340° C., about 350°C., about 360° C., about 370° C., about 380° C., about 390° C., or about400° C., for a period of time of 30 minutes.

In some embodiments, the portion of the coated glass container with thelubricous coating may have a coefficient of friction of less than orequal to about 0.7 after being submerged in a water bath at atemperature of about 70° C. for 10 minutes. In other embodiments, theportion of the coated glass container with the lubricous coating mayhave a coefficient of friction of less than or equal to about 0.7,(i.e., less than or equal to about 0.6, less than or equal to about 0.5,less than or equal to about 0.4, or even less than or equal to about0.3) after being submerged in a water bath at a temperature of about 70°C. for 5 minutes, 10 minutes, 20 minutes, 30 minutes, 40 minutes, 50minutes, or even 1 hour. In some embodiments, the coefficient offriction of the portion of the coated glass container with the lubricouscoating may not increase by more than about 30% after being submerged ina water bath at a temperature of about 70° C. for 10 minutes. In otherembodiments, coefficient of friction of the portion of the coated glasscontainer with the lubricous coating may not increase by more than about30% (i.e., about 25%, about 20%, about 15%, or event about 10%) afterbeing submerged in a water bath at a temperature of about 70° C. for 5minutes, 10 minutes, 20 minutes, 30 minutes, 40 minutes, 50 minutes, oreven 1 hour. In some embodiments, the coefficient of friction of theportion of the coated glass container with the lubricous coating may notincrease at all after being submerged in a water bath at a temperatureof about 70° C. for 5 minutes, 10 minutes, 20 minutes, 30 minutes, 40minutes, 50 minutes, or even 1 hour.

In some embodiments, the portion of the coated glass container with thelubricous coating may have a coefficient of friction of less than orequal to about 0.7 after exposure to lyophilization conditions. In otherembodiments, the portion of the coated glass container with thelubricous coating may have a coefficient of friction of less than orequal to about 0.7, (i.e., less than or equal to about 0.6, less than orequal to about 0.5, less than or equal to about 0.4, or even less thanor equal to about 0.3) after exposure to lyophilization conditions. Insome embodiments, the coefficient of friction of the portion of thecoated glass container with the lubricous coating may not increase bymore than about 30% after exposure to lyophilization conditions. Inother embodiments, coefficient of friction of the portion of the coatedglass container with the lubricous coating may not increase by more thanabout 30% (i.e., about 25%, about 20%, about 15%, or event about 10%)after exposure to lyophilization conditions. In some embodiments, thecoefficient of friction of the portion of the coated glass containerwith the lubricous coating may not increase at all after exposure tolyophilization conditions.

In some embodiments, the portion of the coated glass container with thelubricous coating may have a coefficient of friction of less than orequal to about 0.7 after exposure to autoclave conditions. In otherembodiments, the portion of the coated glass container with thelubricous coating may have a coefficient of friction of less than orequal to about 0.7, (i.e., less than or equal to about 0.6, less than orequal to about 0.5, less than or equal to about 0.4, or even less thanor equal to about 0.3) after exposure to autoclave conditions. In someembodiments, the coefficient of friction of the portion of the coatedglass container with the lubricous coating may not increase by more thanabout 30% after exposure to autoclave conditions. In other embodiments,coefficient of friction of the portion of the coated glass containerwith the lubricous coating may not increase by more than about 30%(i.e., about 25%, about 20%, about 15%, or event about 10%) afterexposure to autoclave conditions. In some embodiments, the coefficientof friction of the portion of the coated glass container with thelubricous coating may not increase at all after exposure to autoclaveconditions.

In some embodiments, after the glass container 100 with the lubricouscoating 160 is abraded by an identical glass container with a 30 Nnormal force, the coefficient of friction of the abraded area of theglass container 100 does not increase by more than about 20% followinganother abrasion by an identical glass container with a 30 N normalforce at the same spot. In other embodiments, after the glass container100 with the lubricous coating 160 is abraded by an identical glasscontainer with a 30 N normal force, the coefficient of friction of theabraded area of the glass container 100 does not increase by more thanabout 15% or even 10% following another abrasion by an identical glasscontainer with a 30 N normal force at the same spot. However, it is notnecessary that all embodiments of the glass container 100 with thelubricous coating 160 display such properties.

The coated glass containers described herein have a horizontalcompression strength. The horizontal compression strength, as describedherein, is measured by a horizontal compression apparatus 500, which isschematically depicted in FIG. 4. The coated glass container 100 istested by positioning the container horizontally between two platens 502a, 502 b which are oriented in parallel to the long axis of the glasscontainer, as shown in FIG. 4. A mechanical load 504 is then applied tothe coated glass container 100 with the platens 502 a, 502 b in thedirection perpendicular to the long axis of the glass container. Theload rate for vial compression is 0.5 in/min, meaning that the platensmove towards each other at a rate of 0.5 in/min. The horizontalcompression strength is measured at 25° C. and 50% relative humidity. Ameasurement of the horizontal compression strength can be given as afailure probability at a selected normal compression load. As usedherein, failure occurs when the glass container ruptures under ahorizontal compression in least 50% of samples. In some embodiments, acoated glass container may have a horizontal compression strength atleast 10%, 20%, or 30% greater than an uncoated vial.

Referring now to FIGS. 8 and 9, the horizontal compression strengthmeasurement may also be performed on an abraded glass container.Specifically, operation of the testing jig 300 may create damage on thecoated glass container outer surface, such as a surface scratch orabrasion that weakens the strength of the coated glass container 100.The glass container is then subjected to the horizontal compressionprocedure described above, wherein the container is placed between twoplatens with the scratch pointing outward parallel to the platens. Thescratch can be characterized by the selected normal pressure applied bya vial-on-vial jig and the scratch length. Unless identified otherwise,scratches for abraded glass containers for the horizontal compressionprocedure are characterized by a scratch length of 20 mm created by anormal load of 30 N.

The coated glass containers can be evaluated for horizontal compressionstrength following a heat treatment. The heat treatment may be exposureto a temperature of about 250° C., about 260° C., about 270° C., about280° C., about 290° C., about 300° C., about 310° C., about 320° C.,about 330° C., about 340° C., about 350° C., about 360° C., about 370°C., about 380° C., about 390° C., or about 400° C., for a period of timeof 30 minutes. In some embodiments, the horizontal compression strengthof the coated glass container is not reduced by more than about 20%,30%, or even 40% after being exposed to a heat treatment, such as thosedescribed above, and then being abraded, as described above. In oneembodiment, the horizontal compression strength of the coated glasscontainer is not reduced by more than about 20% after being exposed to aheat treatment of about 250° C., about 260° C., about 270° C., about280° C., about 290° C., about 300° C., about 310° C., about 320° C.,about 330° C., about 340° C., about 350° C., about 360° C., about 370°C., about 380° C., about 390° C., or about 400° C., for a period of timeof 30 minutes, and then being abraded.

In some other embodiments, the glass container 100 with the lubricouscoating 160 may be thermally stable at elevated temperatures. The phrase“thermally stable,” as used herein, means that the lubricous coating 160applied to the glass container remains substantially intact on thesurface of the glass container after exposure to the elevatedtemperatures such that, after exposure, the mechanical properties of thecoated glass container, specifically the coefficient of friction and thehorizontal compression strength, are only minimally affected, if at all.This indicates that the lubricous coating remains adhered to the surfaceof the glass following elevated temperature exposure and continues toprotect the glass container from mechanical insults such as abrasions,impacts and the like. The glass containers with lubricous coatingsdescribed herein may be thermally stable after heating to a temperatureof at least about 250° C. or even about 260° C. for a time period of 30minutes.

In the embodiments described herein, a glass container with a lubricouscoating (i.e., the coated glass container) is considered to be thermallystable if the coated glass container meets both a coefficient offriction standard and a horizontal compression strength standard afterheating to the specified temperature and remaining at that temperaturefor the specified time. To determine if the coefficient of frictionstandard is met, the coefficient of friction of a first coated glasscontainer is determined in as-received condition (i.e., prior to anythermal exposure) using the testing jig depicted in FIG. 9 and a 30 Napplied load. A second coated glass container (i.e., a glass containerhaving the same glass composition and the same coating composition asthe first coated glass container) is thermally exposed under theprescribed conditions and cooled to room temperature. Thereafter, thecoefficient of friction of the second glass container is determinedusing the testing jig depicted in FIG. 9 to abrade the coated glasscontainer with a 30 N applied load resulting in an abraded (i.e., a“scratch”) having a length of approximately 20 mm. If the coefficient offriction of the second coated glass container is less than 0.7 and thesurface of the glass of the second glass container in the abraded areadoes not have any observable damage, then the coefficient of frictionstandard is met for purposes of determining the thermal stability of thelubricous coating. The term “observable damage,” as used herein meansthat the surface of the glass in the abraded area of the glass containerhas less than six glass checks per 0.5 cm of length of the abraded areawhen observed with a Nomarski or differential interference contrast(DIC) spectroscopy microscope at a magnification of 100× with LED orhalogen light sources. A standard definition of a glass check or glasschecking is described in G. D. Quinn, “NIST Recommended Practice Guide:Fractography of Ceramics and Glasses,” NIST special publication 960-17(2006).

To determine if the horizontal compression strength standard is met, afirst coated glass container is abraded in the testing jig depicted inFIG. 9 under a 30 N load to form a 20 mm scratch. The first coated glasscontainer is then subjected to a horizontal compression test, asdescribed herein, and the retained strength of the first coated glasscontainer is determined. A second coated glass container (i.e., a glasscontainer having the same glass composition and the same coatingcomposition as the first coated glass container) is thermally exposedunder the prescribed conditions and cooled to room temperature.Thereafter, the second coated glass container is abraded in the testingjig depicted in FIG. 9 under a 30 N load. The second coated glasscontainer is then subjected to a horizontal compression test, asdescribed herein, and the retained strength of the second coated glasscontainer is determined. If the retained strength of the second coatedglass container does not decrease by more than about 20% relative to thefirst coated glass container then the horizontal compression strengthstandard is met for purposes of determining the thermal stability of thelubricous coating.

In the embodiments described herein, the coated glass containers areconsidered to be thermally stable if the coefficient of frictionstandard and the horizontal compression strength standard are met afterexposing the coated glass containers to a temperature of at least about250° C. or even about 260° C. for a time period of about 30 minutes(i.e., the coated glass containers are thermally stable at a temperatureof at least about 250° C. or even about 260° C. for a time period ofabout 30 minutes). The thermal stability may also be assessed attemperatures from about 250° C. up to about 400° C. For example, in someembodiments, the coated glass containers will be considered to bethermally stable if the standards are met at a temperature of at leastabout 270° C. or even about 280° C. for a time period of about 30minutes. In still other embodiments, the coated glass containers will beconsidered to be thermally stable if the standards are met at atemperature of at least about 290° C. or even about 300° C. for a timeperiod of about 30 minutes. In further embodiments, the coated glasscontainers will be considered to be thermally stable if the standardsare met at a temperature of at least about 310° C. or even about 320° C.for a time period of about 30 minutes. In still other embodiments, thecoated glass containers will be considered to be thermally stable if thestandards are met at a temperature of at least about 330° C. or evenabout 340° C. for a time period of about 30 minutes. In yet otherembodiments, the coated glass containers will be considered to bethermally stable if the standards are met at a temperature of at leastabout 350° C. or even about 360° C. for a time period of about 30minutes. In some other embodiments, the coated glass containers will beconsidered to be thermally stable if the standards are met at atemperature of at least about 370° C. or even about 380° C. for a timeperiod of about 30 minutes. In still other embodiments, the coated glasscontainers will be considered to be thermally stable if the standardsare met at a temperature of at least about 390° C. or even about 400° C.for a time period of about 30 minutes.

The coated glass containers disclosed herein may also be thermallystable over a range of temperatures, meaning that the coated glasscontainers are thermally stable by meeting the coefficient of frictionstandard and horizontal compression strength standard at eachtemperature in the range. For example, in the embodiments describedherein, the coated glass containers may be thermally stable from atleast about 250° C. or even about 260° C. to a temperature of less thanor equal to about 400° C. In some embodiments, the coated glasscontainers may be thermally stable in a range from at least about 250°C. or even about 260° C. to about 350° C. In some other embodiments, thecoated glass containers may be thermally stable from at least about 280°C. to a temperature of less than or equal to about 350° C. In stillother embodiments, the coated glass containers may be thermally stablefrom at least about 290° C. to about 340° C. In another embodiment, thecoated glass container may be thermally stable at a range oftemperatures of about 300° C. to about 380° C. In another embodiment,the coated glass container may be thermally stable at a range oftemperatures from about 320° C. to about 360° C.

Mass loss refers to a measurable property of the coated glass containerwhich relates to the amount of volatiles liberated from the coated glasscontainer when the coated glass container is exposed to a selectedelevated temperature for a selected period of time. Mass loss isgenerally indicative of the mechanical degradation of the coating due tothermal exposure. Since the glass body of the coated glass containerdoes not exhibit measurable mass loss at the measured temperatures, themass loss test, as described in detail herein, yields mass loss data foronly the lubricous coating that is applied to the glass container.Multiple factors may affect mass loss. For example, the amount oforganic material that can be removed from the coating may affect massloss. The breakdown of carbon backbones and side chains in a polymerwill result in a theoretical 100% removal of the coating. Organometallicpolymer materials typically lose their entire organic component, but theinorganic component remains behind. Thus, mass loss results arenormalized based upon how much of the coating is organic and inorganic(e.g., % silica of the coating) upon complete theoretical oxidation.

To determine the mass loss, a coated sample, such as a coated glasscontainer, is initially heated to 150° C. and held at this temperaturefor 30 minutes to dry the coating, effectively driving off H₂O from thecoating. The sample is then heated from 150° C. to 350° C. at a ramprate of 10° C./min in an oxidizing environment, such as air. Forpurposes of mass loss determination, only the data collected from 150°C. to 350° C. is considered. In some embodiments, the lubricous coatinghas a mass loss of less than about 5% of its mass when heated from atemperature of 150° C. to 350° C. at a ramp rate of about 10° C./minute.In other embodiments, the lubricous coating has a mass loss of less thanabout 3% or even less than about 2% when heated from a temperature of150° C. to 350° C. at a ramp rate of about 10° C./minute. In some otherembodiments, the lubricous coating has a mass loss of less than about1.5% when heated from a temperature of 150° C. to 350° C. at a ramp rateof about 10° C./minute. In some other embodiments, the lubricous coatinghas a mass loss of less than about 0.75% when heated from a temperatureof 150° C. to 350° C. at a ramp rate of about 10° C./minute. In someother embodiments, the lubricous coating loses substantially none of itsmass when heated from a temperature of 150° C. to 350° C. at a ramp rateof about 10° C./minute.

Mass loss results are based on a procedure wherein the weight of acoated glass container is compared before and after a heat treatment,such as a ramping temperature of 10°/minute from 150° C. to 350° C., asdescribed herein. The difference in weight between the pre-heattreatment and post-heat treatment vial is the weight loss of thecoating, which can be standardized as a percent weight loss of thecoating such that the pre-heat treatment weight of the coating (weightnot including the glass body of the container and following thepreliminary heating step) is known by comparing the weight on anuncoated glass container with a pre-treatment coated glass container.Alternatively, the total mass of coating may be determined by a totalorganic carbon test or other like means.

Referring now to FIG. 10, outgassing refers to a measurable property ofthe coated glass container 100 which relates to the amount of volatilesliberated from the coated glass container 100 when the coated glasscontainer is exposed to a selected elevated temperature for a selectedperiod of time. Outgassing measurements are reported herein as an amountby weight of volatiles liberated per the surface area of the glasscontainer having the coating during exposure to the elevated temperaturefor a time period. Since the glass body of the coated glass containerdoes not exhibit measurable outgassing at the temperatures reported foroutgassing, the outgassing test, as described in detail above, yieldsoutgassing data for substantially only the lubricous coating that isapplied to the glass container. Outgassing results are based on aprocedure wherein a coated glass container 100 is placed in a glasssample chamber 402 of the apparatus 400 depicted in FIG. 10. Abackground sample of the empty sample chamber is collected prior to eachsample run. The sample chamber is held under a constant 100 ml/min airpurge as measured by rotometer 406 while the furnace 404 is heated to350° C. and held at that temperature for 1 hour to collect the chamberbackground sample. Thereafter, the coated glass container 100 ispositioned in the sample chamber 402 and the sample chamber is heldunder a constant 100 ml/min air purge and heated to an elevatedtemperature and held at temperature for a period of time to collect asample from a coated glass container 100. The glass sample chamber 402is made of Pyrex, limiting the maximum temperature of the analysis to600° C. A Carbotrap 300 adsorbent trap 408 is assembled on the exhaustport of the sample chamber to adsorb the resulting volatile species asthey are released from the sample and are swept over the absorbent resinby the air purge gas 410 where the volatile species are adsorbed. Theabsorbent resin is then placed directly into a Gerstel ThermalDesorption unit coupled directly to a Hewlett Packard 5890 Series II gaschromatograph/Hewlett Packard 5989 MS engine. Outgassing species arethermally desorbed at 350° C. from the adsorbent resin and cryogenicallyfocused at the head of a non-polar gas chromatographic column (DB-5MS).The temperature within the gas chromatograph is increased at a rate of10° C./min to a final temperature of 325° C., so as to provide for theseparation and purification of volatile and semi-volatile organicspecies. The mechanism of separation has been demonstrated to be basedon the heats of vaporization of different organic species resulting in,essentially, a boiling point or distillation chromatogram. Followingseparation, purified species are analyzed by traditional electron impactionization mass spectrometric protocols. By operating under standardizedconditions, the resulting mass spectra may be compared with existingmass spectral libraries.

In some embodiments, the coated glass containers described hereinexhibit an outgas sing of less than or equal to about 54.6 ng/cm², lessthan or equal to about 27.3 ng/cm², or even less than or equal to about5.5 ng/cm² during exposure to elevated temperature of about, 250° C.,about 275° C., about 300° C., about 320° C., about 360° C., or evenabout 400° C. for time periods of about 15 minutes, about 30 minutes,about 45 minutes, or about 1 hour. Furthermore, the coated glasscontainers may be thermally stable in a specified range of temperatures,meaning that the coated containers exhibit a certain outgassing, asdescribed above, at every temperature within the specified range. Priorto outgassing measurements, the coated glass containers may be inas-coated condition (i.e., immediately following application of thelubricous coating) or following any one of depyrogenation,lyophilization, or autoclaving. In some embodiments, the coated glasscontainer 100 may exhibit substantially no outgassing.

In some embodiments, outgassing data may be used to determine mass lossof the lubricous coating. A pre-heat treatment coating mass can bedetermined by the thickness of the coating (determined by SEM image orother manner), the density of the lubricous coating, and the surfacearea of the lubricous coating. Thereafter, the coated glass containercan be subjected to the outgassing procedure, and mass loss can bedetermined by finding the ratio of the mass expelled in outgassing tothe pre-heat treatment mass.

The coated glass containers described herein have a four point bendstrength. To measure the four point bend strength of a glass container,a glass tube that is the precursor to the coated glass container 100 isutilized for the measurement. The glass tube has a diameter that is thesame as the glass container but does not include a glass container baseor a glass container mouth (i.e., prior to forming the tube into a glasscontainer). The glass tube is then subjected to a four point bend stresstest to induce mechanical failure. The test is performed at 50% relativehumidity with outer contact members spaced apart by 9″ and inner contactmembers spaced apart by 3″ at a loading rate of 10 mm/min.

The four point bend stress measurement may also be performed on a coatedand abraded tube. Operation of the testing jig 300 may create anabrasion on the tube surface such as a surface scratch that weakens thestrength of the tube, as described in the measurement of the horizontalcompression strength of an abraded vial. The glass tube is thensubjected to a four point bend stress test to induce mechanical failure.The test is performed at 25° C. and at 50% relative humidity using outerprobes spaced apart by 9″ and inner contact members spaced apart by 3″at a loading rate of 10 mm/min, while the tube is positioned such thatthe scratch is put under tension during the test.

In some embodiments, the four point bend strength of a glass tube with alubricous coating after abrasion shows on average at least 10%, 20%, oreven 50% higher mechanical strength than that for an uncoated glass tubeabraded under the same conditions.

Referring to FIG. 11 the transparency and color of the coated containermay be assessed by measuring the light transmission of the containerwithin a range of wavelengths between 400-700 nm using aspectrophotometer. The measurements are performed by directing a lightbeam onto the container normal to the container wall such that the beampasses through the lubricous coating twice, first when entering thecontainer and then when exiting it. In some embodiments, the lighttransmission through the coated glass container may be greater than orequal to about 55% of a light transmission through an uncoated glasscontainer for wavelengths from about 400 nm to about 700 nm. Asdescribed herein, a light transmission can be measured before a thermaltreatment or after a thermal treatment, such as the heat treatmentsdescribed herein. For example, for each wavelength of from about 400 nmto about 700 nm, the light transmission may be greater than or equal toabout 55% of a light transmission through an uncoated glass container.In other embodiments, the light transmission through the coated glasscontainer is greater than or equal to about 55%, about 60%, about 65%,about 70%, about 75%, about 80%, or even about 90% of a lighttransmission through an uncoated glass container for wavelengths fromabout 400 nm to about 700 nm.

As described herein, a light transmission can be measured before anenvironmental treatment, such as a thermal treatment described herein,or after an environmental treatment. For example, following a heattreatment of about 250° C., about 260° C., about 270° C., about 280° C.,about 290° C., about 300° C., about 310° C., about 320° C., about 330°C., about 340° C., about 350° C., about 360° C., about 370° C., about380° C., about 390° C., or about 400° C., for a period of time of 30minutes, or after exposure to lyophilization conditions, or afterexposure to autoclave conditions, the light transmission through thecoated glass container is greater than or equal to about 55%, about 60%,about 65%, about 70%, about 75%, about 80%, or even about 90% of a lighttransmission through an uncoated glass container for wavelengths fromabout 400 nm to about 700 nm

In some embodiments, the coated glass container 100 may be perceived ascolorless and transparent to the naked human eye when viewed at anyangle. In some other embodiments, the lubricous coating 160 may have aperceptible tint, such as when the lubricous coating 160 comprises apolyimide formed from poly(pyromelliticdianhydride-co-4,4′-oxydianiline) amic acid commercially available fromAldrich.

In some embodiments, the glass container 100 with the lubricous coating160 may have an outer surface that is capable of receiving an adhesivelabel. That is, while the lubricous coating 160 has a low coefficient offriction, the coating is still able to receive an adhesive label suchthat the adhesive label is securely attached. However, the ability ofattachment of an adhesive label is not a requirement for all embodimentsof the glass container 100 with the lubricous coating 160 describedherein.

Referring again to FIG. 8, in some embodiments, the lubricous coating160 may be a transient coating. The phrase “transient coating,” as usedherein, means that the coating is not permanently adhered to the glasscontainer 100 and may be removed from the glass container 100 such as bywashing, heating (i.e., pyrolization) or the like. For example, inembodiments where the lubricous coating 160 is a transient coating whichmay be removed by pyrolysis, the coating may pyrolize at temperaturesless than or equal to about 300° C. Alternatively, the lubricous coating160 may be a transient coating that may be removed by washing the glasscontainer with a solution of detergent and water.

In the embodiments described herein, the glass container may be coatedwith inorganic coatings, transient organic coatings, and/or tenaciousorganic coatings in order to achieve the desired low coefficient offriction and resistance to damage.

Inorganic Coating

Still referring to FIG. 8, in some embodiments described herein, thelubricous coating 160 is an inorganic coating. The inorganic coating maybe a tenacious inorganic coating which is permanently adhered to theouter surface 106 of the body 102 of the glass container. The propertiesof the tenacious inorganic coating are not degraded by exposure toelevated temperatures and, as such, the coefficient of friction andhorizontal compression strength of the glass container with thetenacious inorganic coating are substantially the same before and afterexposure to elevated temperatures including, without limitation,temperatures in the range from about 250° C. to about 400° C. Thetenacious inorganic coating is a continuous coating applied to at leasta portion of the outer surface of the body and is generally insoluble inwater and/or organic solvents. For example, in some embodiments, thetenacious inorganic coating may comprise a metal nitride coating, ametal sulfide coating, a metal oxide coating, SiO₂, diamond-like carbon,or a carbide coating. For example, the tenacious inorganic coating mayinclude at least one of TiN, BN, hBN, TiO₂, Ta₂O₅, HfO₂, Nb₂O₅, V₂O₅,SnO, SnO₂, ZrO₂, Al₂O₃, SiO₂, ZnO, MoS₂, BC, SiC, or similar metaloxide, metal nitride and carbide coatings which exhibit a relatively lowcoefficient of friction relative to a like-coated glass container aswell as having relatively high thermal stabilities. In theseembodiments, the coatings may be applied to the outer surface of theglass container by physical vapor deposition methods such asevaporation, electron beam evaporation, dc magnetron sputtering,unbalanced dc magnetron sputtering, ac magnetron sputtering, andunbalanced ac magnetron sputtering. Alternatively, the coatings may beapplied by powder coating. Chemical vapor deposition (CVD) techniquesmay also be used to apply the coatings including ultrahigh vacuum CVD,low pressure CVD, atmospheric pressure CVD, metal-organic CVD, laserCVD, photochemical CVD, aerosol assisted CVD, microwave plasma assistedCVD, plasma-enhanced CVD, direct liquid injection CVD, atomic layer CVD,combustion CVD, Hot wire CVD, rapid thermal CVD, chemical vaporinfiltration, and chemical beam epitaxy.

In one particular embodiment, the tenacious inorganic coating isdiamond-like carbon. Films or coatings formed from diamond-like carbongenerally exhibit a low coefficient of friction and high hardness.Specifically, a significant amount of the carbon in DLC coatings is SP3hybridized carbon. This material imparts some properties of a diamond tothese coatings, as high hardness and superior wear resistance. Thehardness of the DLC coatings is directly proportional to the content ofSP3 hybridized content. The DLC coatings may be deposited on the outersurface of the glass container by ion beam deposition, cathodic arcspray, pulsed laser ablation, argon ion sputtering, and plasma-enhancedchemical vapor deposition. Depending on the thickness of the depositedDLC coating, the specific method of deposition, and the composition ofthe coating, the color of the deposited layer can vary from opticallytransparent yellow (i.e., a 0.1 μm thick film of DLC may be opticallytransparent with a slight yellow cast) to amber and black.

Alternatively, the lubricous coating 160 may be an inorganic coatingwhich is temporarily affixed to the outer surface of the glasscontainer, such as a transient coating. In these embodiments, thetransient coating may include an inorganic salt such as MgSO₄, CaSO₄,Ca₃(PO₄)₂, Mg₃(PO₄)₂, KNO₃, K₃PO₄ or the like.

Organic Coatings

In some alternative embodiments, the lubricous coating 160 may be anorganic coating, such as a transient coating temporarily affixed to theouter surface of the glass container or a tenacious organic coatingwhich is permanently affixed to the outer surface of the glasscontainer.

With respect to the organic transient coatings, it is desirable toprotect the surfaces of glass articles (such as glass container or thelike) from damage during manufacture in order to mitigate the reductionin the mechanical strength of the glass due to surface flaws caused bycontact with the glass. This is generally achieved by applying a coatinghaving a low coefficient of friction, as described above. However,because the glass container may be subject to further processing, thecoating does not need to be permanently adhered to the outer surface ofthe glass container and, instead, may be removed in downstreamprocessing steps after the coating has served its purpose of protectingthe glass article. For example, the transient coating may be removed bypyrolysis. In the embodiments described herein, the transient coatingmay be pyrolized at temperatures less than or equal to 300° C. in a timeperiod of less than or equal to 1 hour. Alternatively, the transientcoating may be pyrolized at temperatures of 265° C. for 2.5 hours oreven at 360° C. for 10 minutes or less.

Various organic materials may be utilized to form the transient coating.For example, in some embodiments, the transient coating may comprise,for example, a mixture of polyoxyethylene glycol, methacrylate resin,melamine formaldehyde resin, and polyvinyl alcohol as disclosed in U.S.Pat. No. 3,577,256. Such a coating may be applied to the outer surfaceof the glass container after formation and may be pyrolized from theglass surface in the annealing lehr.

In another embodiment, the transient organic coating may comprise one ormore polysaccharides, as disclosed in U.S. Pat. No. 6,715,316B2 whichdescribes removable protective coatings. Such coatings can be removedfrom the glass surface using a mild, water-based detergent, such as, forexample 2% Semiclean KG in water.

In another embodiment, the transient organic coating may be a “cold-end”coating as described in U.S. Pat. No. 4,055,441 or similar coatings.Such coatings may be formed from at least one of poly(ethylene oxides),poly (propylene oxides), ethylene oxide-propylene oxide copolymers,polyvinyl-pyrolidinones, polyethyleneimines, poly(methyl vinyl ethers),polyacrylamides, polymethacrylamides, polyurethanes,poly(vinylacetates), polyvinyl formal, polyformaldehydes includingpolyacetals and acetal copolymers, poly(alkyl methacrylates), methylcelluloses, ethyl celluloses, hydroxyethyl celluloses, hydroxypropylcelluloses, sodium carboxymethyl celluloses, methyl hydroxypropylcelluloses, poly (acrylic acids) and salts thereof, poly(methacrylicacids) and salts thereof, ethylene-maleic anhydride copolymers,ethylene-vinyl alcohol copolymers, ethylene-acrylic acid copolymers,vinyl acetate-vinyl alcohol copolymers, methyl vinyl ether-maleicanhydride copolymers, emulsifiable polyurethanes, polyoxyethylenestearates, and polyolefins including polyethylenes, polypropylenes andcopolymers thereof, starches and modified starches, hydrocolloids,polyacryloamide, vegetable and animal fats, wax, tallow, soap,stearine-paraffin emulsions, polysiloxanes of dimethyl or diphenyl ormethyl/phenyl mixtures, perfluorinated siloxanes and other substitutedsiloxanes, alkylsilanes, aromatic silanes, and oxidized polyethylene,combinations thereof, or similar coatings.

The transient organic coatings may be applied by contacting such acoating directly with the glass container. For example, the coating maybe applied by a submersion process, or alternatively, by a spray orother suitable means. The coating may then be dried, and, optionally,cured at high temperatures.

Referring now to FIGS. 8 and 12A, in some embodiments, the lubricouscoating 160 is a tenacious organic coating adhered to at least a portionof the outer surface 106 of the glass body 102. The tenacious organiccoating has a low coefficient of friction and is also thermally stableat elevated temperatures, as described above. The lubricous coating 160has an outer surface 162 and a glass contacting surface 164. Inembodiments where the lubricous coating 160 is a tenacious organiccoating, the lubricous coating 160 may comprise a coupling agent layer180 that is in direct contact with the outer surface 106 of the glassbody 102 and a polymer layer 170 that is in direct contact with thecoupling agent layer 180. However, it should be understood that, in someembodiments, the lubricous coating 160 may not include a coupling agentlayer 180 and the polymer layer 170 may be in direct contact with theouter surface 106 of the glass body 102. In some embodiments, thelubricous coating 160 is a coating layer as described in U.S.Provisional application Ser. No. 13/780,754 filed Feb. 28, 2013 andentitled “Glass Articles with Low Friction Coatings”, the entirety ofwhich is incorporated herein by reference.

Now referring to FIGS. 8 and 12A, in one embodiment, the lubricouscoating 160 comprises a bi-layered structure. FIG. 12A shows a crosssection of a portion of a coated glass container where the lubricouscoating 160 comprises a polymer layer 170 and a coupling agent layer180. A polymer chemical composition may be contained in polymer layer170 and a coupling agent may be contained in a coupling agent layer 180.The coupling agent layer 180 may be in direct contact with the outersurface 106 of the glass body 102. The polymer layer 170 may be indirect contact with the coupling agent layer 180 and may form the outersurface 162 of the lubricous coating 160. In some embodiments thecoupling agent layer 180 is bonded to the outer surface 106 of the glassbody 102 and the polymer layer 170 is bonded to the coupling agent layer180 at an interface 174. However, it should be understood that, in someembodiments, the lubricous coating 160 may not include a coupling agent,and the polymer chemical composition may be disposed in a polymer layer170 in direct contact with the outer surface 106 of the of the glassbody 102. In another embodiment, the polymer chemical composition andcoupling agent may be substantially mixed in a single layer. In someother embodiments, the polymer layer 170 may be positioned over thecoupling agent layer 180, meaning that the polymer layer 170 is in anouter layer relative to the coupling agent layer 180, and the outersurface 106 of the glass body 102. As used herein, a first layerpositioned “over” a second layer means that the first layer could be indirect contact with the second layer or separated from the second layer,such as with a third layer disposed between the first and second layers.

Referring now to FIG. 12B, in one embodiment, the lubricous coating 160may further comprise an interface layer 190 positioned between thecoupling agent layer 180 and the polymer layer 170. The interface layer190 may comprise one or more chemical compositions of the polymer layer170 bound with one or more of the chemical compositions of the couplingagent layer 180. In this embodiment, the interface of the coupling agentlayer 180 and polymer layer 170 forms an interface layer 190 wherebonding occurs between the polymer chemical composition and the couplingagent. However, it should be understood that in some embodiments, theremay be no appreciable layer at the interface of the coupling agent layer180 and polymer layer 170 where the polymer and coupling agent arechemically bound to one another as described above with reference toFIG. 12A.

In another embodiment, the polymer chemical composition and couplingagent may be substantially mixed in a single layer, forming a homogenouslayer of lubricous coating. Such a mixed single layer may be in directcontact with the outer surface 106 of the glass body 102. As describedherein, the materials of the polymer layer 170 and coupling agent layer180 (i.e., at least a polymer and at least a coupling agent,respectively) may be mixed to form at least one layer of a lubricouscoating 160. The mixed-layer lubricous coating 160 may additionallycomprise materials other than a polymer chemical composition and acoupling agent. To form the mixed layer lubricous coating 160, thevarious materials of such a layer may be mixed together in solutionprior to the application of the lubricous coating 160 onto the glasscontainer 100. In other embodiments, mixed layers may be over or undernon-mixed layers, such as, for example, a mixed layer of polymer andcoupling agent under a layer of substantially only polymer material. Inother embodiments, the lubricous coating may comprise more than twolayers, such as three or four layers.

The lubricous coating 160 applied to the outer surface 106 of the glassbody 102 may have a thickness of less than about 100 μm or even lessthan or equal to about 1 μm. In some embodiments, the thickness of thelubricous coating 160 may be less than or equal to about 100 nm thick.In other embodiments, the lubricous coating 160 may be less than about90 nm thick, less than about 80 nm thick, less than about 70 nm thick,less than about 60 nm thick, less than about 50 nm, or even less thanabout 25 nm thick. In some embodiments, the lubricous coating 160 maynot be of uniform thickness over the entirety of the glass body 102. Forexample, the coated glass container 100 may have a thicker lubricouscoating 160 in some areas, due to the process of contacting the outersurface 106 of the glass body 102 with one or more coating solutionsthat form the lubricous coating 160. In some embodiments, the lubricouscoating 160 may have a non-uniform thickness. For example, the coatingthickness may be varied over different regions of a coated glasscontainer 100, which may promote protection in a selected region. Inanother embodiment, only selected portions of the outer surface 106 ofthe glass body are coated with a lubricous coating 160.

In embodiments which include at least two layers, such as a polymerlayer 170, interface layer 190, and/or coupling agent layer 180, eachlayer may have a thickness of less than about 100 μm or even less thanor equal to about 1 μm. In some embodiments, the thickness of each layermay be less than or equal to about 100 nm. In other embodiments, eachlayer may be less than about 90 nm thick, less than about 80 nm thick,less than about 70 nm thick, less than about 60 nm thick, less thanabout 50 nm, or even less than about 25 nm thick.

As noted herein, in some embodiments, the lubricous coating 160comprises a coupling agent. The coupling agent may improve the adhesionor bonding of the polymer chemical composition to the outer surface 106of the glass body 102, and is generally disposed between the glass body102 and the polymer chemical composition in a polymer chemicalcomposition layer 170, or mixed with the polymer chemical composition.Adhesion, as used herein, refers to the strength of adherence or bondingof the polymer layer prior to and following a treatment applied to thecoated glass container, such as a thermal treatment. Thermal treatmentsinclude, without limitation, autoclaving, depyrogenation,lyophilization, or the like.

In one embodiment, the coupling agent may comprise at least one silanechemical composition. As used herein, a “silane” chemical composition isany chemical composition comprising a silane moiety, includingfunctional organosilanes, as well as silanols formed from silanes inaqueous solutions. The silane chemical compositions of the couplingagent may be aromatic or aliphatic. In some embodiments, the at leastone silane chemical composition may comprise an amine moiety, such as aprimary amine moiety or a secondary amine moiety. Furthermore, thecoupling agent may comprise hydrolysates and/or oligomers of suchsilanes, such as one or more silsesquioxane chemical compositions thatare formed from the one or more silane chemical compositions. Thesilsesquioxane chemical compositions may comprise a full cage structure,partial cage structure, or no cage structure.

The coupling agent may comprise any number of different chemicalcompositions, such as one chemical composition, two different chemicalcompositions, or more than two different chemical compositions includingoligomers formed from more than one monomeric chemical composition. Inone embodiment, the coupling agent may comprise at least one of (1) afirst silane chemical composition, hydrolysate thereof, or oligomerthereof, and (2) a chemical composition formed from the oligomerizationof at least the first silane chemical composition and a second silanechemical composition. In another embodiment, the coupling agentcomprises a first and second silane. As used herein, a “first” silanechemical composition and a “second” silane chemical composition aresilanes having different chemical compositions. The first silanechemical composition may be an aromatic or an aliphatic chemicalcomposition, may optionally comprise an amine moiety, and may optionallybe an alkoxysilane. Similarly, the second silane chemical compositionmay be an aromatic or an aliphatic chemical composition, may optionallycomprise an amine moiety, and may optionally be an alkoxysilane.

For example, in one embodiment, only one silane chemical composition isapplied as the coupling agent. In such an embodiment, the coupling agentmay comprise a silane chemical composition, hydrolysate thereof, oroligomer thereof.

In another embodiment, multiple silane chemical compositions may beapplied as the coupling agent. In such an embodiment, the coupling agentmay comprise at least one of (1) a mixture of the first silane chemicalcomposition and a second silane chemical composition, and (2) a chemicalcomposition formed from the oligomerization of at least the first silanechemical composition and the second silane chemical composition.

Referring to the embodiments described above, the first silane chemicalcomposition, second silane chemical composition, or both, may bearomatic chemical compositions. As used herein, an aromatic chemicalcomposition contains one or more six-carbon rings characteristic of thebenzene series and related organic moieties. The aromatic silanechemical composition may be an alkoxysilane such as, but not limited to,a dialkoxysilane chemical composition, hydrolysate thereof, or oligomerthereof, or a trialkoxysilane chemical composition, hydrolysate thereof,or oligomer thereof. In some embodiments, the aromatic silane maycomprise an amine moiety, and may be an alkoxysilane comprising an aminemoiety. In another embodiment, the aromatic silane chemical compositionmay be an aromatic alkoxysilane chemical composition, an aromaticacyloxysilane chemical composition, an aromatic halogen silane chemicalcomposition, or an aromatic aminosilane chemical composition. In anotherembodiment, the aromatic silane chemical composition may be selectedfrom the group consisting of aminophenyl, 3-(m-aminophenoxy) propyl,N-phenylaminopropyl, or (chloromethy) phenyl substituted alkoxy,acyloxy, halogen, or amino silanes. For example, the aromaticalkoxysilane may be, but is not limited to, aminophenyltrimethoxy silane(sometimes referred to herein as “APhTMS”), aminophenyldimethoxy silane,aminophenyltriethoxy silane, aminophenyldiethoxy silane,3-(m-aminophenoxy) propyltrimethoxy silane, 3-(m-aminophenoxy)propyldimethoxy silane, 3-(m-aminophenoxy) propyltriethoxy silane,3-(m-aminophenoxy) propyldiethoxy silane,N-phenylaminopropyltrimethoxysilane, N-phenylaminopropyldimethoxysilane,N-phenylaminopropyltriethoxysilane, N-phenylaminopropyldiethoxysilane,hydrolysates thereof, or oligomerized chemical composition thereof. Inan exemplary embodiment, the aromatic silane chemical composition may beaminophenyltrimethoxy silane.

Referring again to the embodiments described above, the first silanechemical composition, second silane chemical composition, or both, maybe aliphatic chemical compositions. As used herein, an aliphaticchemical composition is non-aromatic, such as a chemical compositionhaving an open chain structure, such as, but not limited to, alkanes,alkenes, and alkynes. For example, in some embodiments, the couplingagent may comprise a chemical composition that is an alkoxysilane andmay be an aliphatic alkoxysilane such as, but not limited to, adialkoxysilane chemical composition, a hydrolysate thereof, or anoligomer thereof, or a trialkoxysilane chemical composition, ahydrolysate thereof, or an oligomer thereof. In some embodiments, thealiphatic silane may comprise an amine moiety, and may be analkoxysilane comprising an amine moiety, such as anaminoalkyltrialkoxysilane. In one embodiment, an aliphatic silanechemical composition may be selected from the group consisting of3-aminopropyl, N-(2-aminoethyl)-3-aminopropyl, vinyl, methyl,N-phenylaminopropyl, (N-phenylamino)methyl,N-(2-vinylbenzylaminoethyl)-3-aminopropyl substituted alkoxy, acyloxy,halogen, or amino silanes, hydrolysates thereof, or oligomers thereof.Aminoalkyltrialkoxysilanes, include, but are not limited to,3-aminopropyltrimethoxy silane (sometimes referred to herein as “GAPS”),3-aminopropyldimethoxy silane, 3-aminopropyltriethoxy silane,3-aminopropyldiethoxy silane,N-(2-aminoethyl)-3-aminopropyltrimethoxysilane,N-(2-aminoethyl)-3-aminopropyldimethoxysilane,N-(2-aminoethyl)-3-aminopropyltriethoxysilane,N-(2-aminoethyl)-3-aminopropyldiethoxysilane, hydrolysates thereof, andoligomerized chemical composition thereof. In other embodiments, thealiphatic alkoxysilane chemical composition may not contain an aminemoiety, such as an alkyltrialkoxysilane or alkylbialkoxysilane. Suchalkyltrialkoxysilanes or alkylbialkoxysilanes include, but are notlimited to, vinyltrimethoxy silane, vinyldimethoxy silane,vinyltriethoxy silane, vinyldiethoxy silane, methyltrimethoxysilane,methyltdimethoxysilane, methyltriethoxysilane, methyldiethoxysilane,hydrolysates thereof, or oligomerized chemical composition thereofincluding amino functional silsesquioxane oligomers such as, but notlimited to, WSA-7011, WSA-9911, WSA-7021, WSAV-6511 manufactured byGelest. In an exemplary embodiment, the aliphatic silane chemicalcomposition is 3-aminopropyltrimethoxy silane.

In another embodiment, the coupling agent layer 180 may comprisechemical species that are hydrolyzed analogs of aminoalkoxysilanes suchas, but not limited to, (3-aminopropyl)silanetriol,N-(2-aminoethyl)-3-aminopropyl-silanetriol and/or mixtures thereof.

In another embodiment, the coupling agent layer 180 may comprise achemical species that is an aminoalkylsilsesquioxane. In one embodimentthe coupling agent layer 180 comprises aminopropylsilsesquioxane (APS)oligomer (commercially available as an aqueous solution from Gelest).

In another embodiment, the coupling agent layer 180 may be an inorganicmaterial, such as metal and/or ceramic film. Non-limiting examples ofsuitable inorganic materials used as the coupling agent layer 180include tin, titanium, and/or oxides thereof.

It has been found that forming the coupling agent from combinations ofdifferent chemical compositions, particularly combinations of silanechemical compositions, may improve the thermal stability of thelubricous coating 160. For example, it has been found that combinationsof aromatic silanes and aliphatic silanes, such as those describedabove, improve the thermal stability of the lubricous coating, therebyproducing a coating which retains its the mechanical properties, such ascoefficient of friction and adhesion performance following a heattreatment at elevated temperatures. Accordingly, in one embodiment thecoupling agent comprises a combination of aromatic and aliphaticsilanes. In these embodiments, the ratio of aliphatic silanes toaromatic silanes (aliphatic:aromatic) may be from about 1:3 to about1:0.2. If the coupling agent comprises two or more chemical composition,such as at least an aliphatic silane and an aromatic silane, the ratioby weight of the two chemical compositions may be any ratio, such as aweight ratio of a first silane chemical composition to a second silanechemical composition (first silane:second silane) of about 0.1:1 toabout 10:1. For example, in some embodiments the ration may be from0.5:1 to about 2:1, such as 2:1, 1:1, 0.5:1. In some embodiments, thecoupling agent may comprise combinations of multiple aliphatic silanesand/or multiple aromatic silanes, which could be applied to the glasscontainer in one or multiple steps with or without organic or inorganicfillers. In some embodiments, the coupling agent comprises oligomers,such as silsesquioxanes, formed from both the aliphatic and aromaticsilanes.

In an exemplary embodiment, the first silane chemical composition is anaromatic silane chemical composition and the second silane chemicalcomposition is an aliphatic silane chemical composition. In oneexemplary embodiment, the first silane chemical composition is anaromatic alkoxysilane chemical composition comprising at least one aminemoiety and the second silane chemical composition is an aliphaticalkoxysilane chemical composition comprising at least one amine moiety.In another exemplary embodiment, the coupling agent comprises anoligomer of one or more silane chemical compositions, wherein theoligomer is a silsesquioxane chemical composition and at least one ofthe silane chemical compositions comprises at least one aromatic moietyand at least one amine moiety. In one particular exemplary embodiment,the first silane chemical composition is aminophenyltrimethoxy silaneand the second silane chemical composition is 3-aminopropyltrimethoxysilane. The ratio of aromatic silane to aliphatic silane may be about1:1. In another particular exemplary embodiment, the coupling agentcomprises an oligomer formed from aminophenyltrimethoxy and3-aminopropyltrimethoxy. In another embodiment, the coupling agent maycomprise both a mixture of aminophenyltrimethoxy and3-aminopropyltrimethoxy and oligomers formed from the two.

In one embodiment, the coupling agent is applied to the outer surface106 of the glass body 102 by contacting the surface with the dilutedcoupling agent by a submersion process. The coupling agent may be mixedin a solvent when applied to the glass body 102. In another embodiment,the coupling agent may be applied to the glass body 102 by a spray orother suitable means. The glass body 102 with coupling agent may then bedried at around 120° C. for about 15 min, or any time and temperaturesufficient to adequately liberate the water and/or other organicsolvents present on the outer surface 106 of the wall portion 110.

Referring to FIG. 12A, in one embodiment, the coupling agent ispositioned on the glass container as a coupling agent layer 180 and isapplied as a solution comprising about 0.5 wt % of a first silane andabout 0.5 wt % of a second silane (total 1 wt % silane) mixed with atleast one of water and an organic solvent, such as, but not limited to,methanol. However, it should be understood that the total silaneconcentration in the solution may be more or less than about 1 wt %,such as from about 0.1 wt % to about 10 wt %, from about 0.3 wt % toabout 5.0 wt %, or from about 0.5 wt % to about 2.0 wt %. For example,in one embodiment, the weight ratio of organic solvent to water (organicsolvent:water) may be from about 90:10 to about 10:90, and, in oneembodiment, may be about 75:25. The weight ratio of silane to solventmay affect the thickness of the coupling agent layer, where increasedpercentages of silane chemical composition in the coupling agentsolution may increase the thickness of the coupling agent layer 180.However, it should be understood that other variables may affect thethickness of the coupling agent layer 180 such as, but not limited, thespecifics of the dip coating process, such as the withdraw speed fromthe bath. For example, a faster withdraw speed may form a thickercoupling agent layer 180.

In one embodiment, the coupling agent layer 180 is applied as a solutioncomprising a first silane chemical species and a second silane chemicalspecies, which may improve the thermal stability and/or the mechanicalproperties of the lubricous coating 160. For example, the first silanechemical species may be an aliphatic silane, such as GAPS, and thesecond silane chemical species may be an aromatic silane, such asAPhTMS. In this example, the ratio of aliphatic silanes to aromaticsilanes (aliphatic:aromatic) may be about 1:1. However, it should beunderstood that other ratios are possible, including from about 1:3 toabout 1:0.2, as described above. The aromatic silane chemical speciesand the aliphatic silane chemical species may be mixed with at least oneof water and an organic solvent, such as, but not limited to, methanol.This solution is then coated on the outer surface 106 of the glass body102 and cured to form the coupling agent layer 180.

In another embodiment, the coupling agent layer 180 is applied as asolution comprising 0.1 vol. % of a commercially availableaminopropylsilsesquioxane oligomer. Coupling agent layer solutions ofother concentrations may be used, including but not limited to,0.01-10.0 vol. % aminopropylsilsesquioxane oligomer solutions.

In some embodiments, the coupling agent layer 180 is sufficientlythermally stable such that the coupling agent layer 180 may, by itself,act as the lubricous coating 160 without any additional coatings, suchas a polymer chemical composition layer 170 or the like. Accordingly, itshould be understood that, in these embodiments, the lubricous coating160 includes a single composition, specifically the coupling agent.

As noted herein, when the lubricous coating 160 is a tenacious organiccoating, the coating may also include a polymer chemical composition asa polymer chemical composition layer 170. The polymer chemicalcomposition may be a thermally stable polymer or mixture of polymers,such as but not limited to, polyimides, polybenzimidazoles,polysulfones, polyetheretheketones, polyetherimides, polyamides,polyphenyls, polybenzothiazoles, polybenzoxazoles, polybisthiazoles, andpolyaromatic heterocyclic polymers with and without organic or inorganicfillers. The polymer chemical composition may be formed from otherthermally stable polymers, such as polymers that do not degrade attemperatures in the range of from 200° C. to 400° C., including 250° C.,300° C., and 350° C. These polymers may be applied with or without acoupling agent.

In one embodiment, the polymer chemical composition is a polyimidechemical composition. If the lubricous coating 160 comprises apolyimide, the polyimide composition may be derived from a polyamicacid, which is formed in a solution by the polymerization of monomers.One such polyamic acid is Novastrat® 800 (commercially available fromNeXolve). A curing step imidizes the polyamic acid to form thepolyimide. The polyamic acid may be formed from the reaction of adiamine monomer, such as a diamine, and an anhydride monomer, such as adianhydride. As used herein, polyimide monomers are described as diaminemonomers and dianhydride monomers. However, it should be understood thatwhile a diamine monomer comprises two amine moieties, in the descriptionthat follows, any monomer comprising at least two amine moieties may besuitable as a diamine monomer. Similarly, it should be understood thatwhile a dianhydride monomer comprises two anhydride moieties, in thedescription that follows any monomer comprising at least two anhydridemoieties may be suitable as a dianhydride monomer. The reaction betweenthe anhydride moieties of the anhydride monomer and amine moieties ofthe diamine monomer forms the polyamic acid. Therefore, as used herein,a polyimide chemical composition that is formed from the polymerizationof specified monomers refers to the polyimide that is formed followingthe imidization of a polyamic acid that is formed from those specifiedmonomers. Generally, the molar ratio of the total anhydride monomers anddiamine monomers may be about 1:1. While the polyimide may be formedfrom only two distinct chemical compositions (one anhydride monomer andone diamine monomer), at least one anhydride monomer may be polymerizedand at least one diamine monomer may be polymerized to from thepolyimide. For example, one anhydride monomer may be polymerized withtwo different diamine monomers. Any number of monomer speciecombinations may be used. Furthermore, the ratio of one anhydridemonomer to a different anhydride monomer, or one or more diamine monomerto a different diamine monomer may be any ratio, such as between about1:0.1 to 0.1:1, such as about 1:9, 1:4, 3:7, 2:3, 1:1, 3:2, 7:3, 4:1 or9:1.

The anhydride monomer from which, along with the diamine monomer, thepolyimide is formed may comprise any anhydride monomer. In oneembodiment, the anhydride monomer comprises a benzophenone structure. Inan exemplary embodiment, benzophenone-3,3′,4,4′-tetracarboxylicdianhydride may be at least one of the anhydride monomer from which thepolyimide is formed. In other embodiments, the diamine monomer may havean anthracene structure, a phenanthrene structure, a pyrene structure,or a pentacene structure, including substituted versions of the abovementioned dianhydrides.

The diamine monomer from which, along with the anhydride monomer, thepolyimide is formed may comprise any diamine monomer. In one embodiment,the diamine monomer comprises at least one aromatic ring moiety. FIGS.13 and 14 show examples of diamine monomers that, along with one or moreselected anhydride monomer, may form the polyimide comprising thepolymer chemical composition. The diamine monomer may have one or morecarbon molecules connecting two aromatic ring moieties together, asshown in FIG. 13, wherein R of FIG. 13 corresponds to an alkyl moietycomprising one or more carbon atoms. Alternatively, the diamine monomermay have two aromatic ring moieties that are directly connected and notseparated by at least one carbon molecule, as shown in FIG. 14. Thediamine monomer may have one or more alkyl moieties, as represented byR′ and R″ in FIGS. 13 and 14. For example, in FIGS. 13 and 14, R′ and R″may represent an alkyl moiety such as methyl, ethyl, propyl, or butylmoieties, connected to one or more aromatic ring moieties. For example,the diamine monomer may have two aromatic ring moieties wherein eacharomatic ring moiety has an alkyl moiety connected thereto and adjacentan amine moiety connected to the aromatic ring moiety. It should beunderstood that R′ and R″, in both FIGS. 13 and 14, may be the samechemical moiety or may be different chemical moieties. Alternatively, R′and/or R″, in both FIGS. 13 and 14, may represent no atoms at all.

Two different chemical compositions of diamine monomers may form thepolyimide. In one embodiment, a first diamine monomer comprises twoaromatic ring moieties that are directly connected and not separated bya linking carbon molecule, and a second diamine monomer comprises twoaromatic ring moieties that are connected with at least one carbonmolecule connecting the two aromatic ring moieties. In one exemplaryembodiment, the first diamine monomer, the second diamine monomer, andthe anhydride monomer have a molar ratio (first diamine monomer:seconddiamine monomer:anhydride monomer) of about 0.465:0.035:0.5. However,the ratio of the first diamine monomer and the second diamine monomermay vary in a range of about 0.01:0.49 to about 0.40:0.10, while theanhydride monomer ratio remains at about 0.5.

In one embodiment, the polyimide composition is formed from thepolymerization of at least a first diamine monomer, a second diaminemonomer, and an anhydride monomer, wherein the first and second diaminemonomers are different chemical compositions. In one embodiment, theanhydride monomer is a benzophenone, the first diamine monomer comprisestwo aromatic rings directly bonded together, and the second diaminemonomer comprises two aromatic rings bonded together with at least onecarbon molecule connecting the first and second aromatic rings. Thefirst diamine monomer, the second diamine monomer, and the anhydridemonomer may have a molar ratio (first diamine monomer: second diaminemonomer:anhydride monomer) of about 0.465:0.035:0.5.

In an exemplary embodiment, the first diamine monomer is ortho-Tolidine,the second diamine monomer is 4,4′-methylene-bis(2-methylaniline), andthe anhydride monomer is benzophenone-3,3′,4,4′-tetracarboxylicdianhydride. The first diamine monomer, the second diamine monomer, andthe anhydride monomer may have a molar ratio (first diaminemonomer:second diamine monomer:anhydride monomer) of about0.465:0.035:0.5.

In some embodiments, the polyimide may be formed from the polymerizationof one or more of: bicyclo[2.2.1]heptane-2,3,5,6-tetracarboxylicdianhydride, cyclopentane-1,2,3,4-tetracarboxylic 1,2;3,4-dianhydride,bicyclo[2.2.2]octane-2,3,5,6-tetracarboxylic dianhydride,4arH,8acH)-decahydro-1t,4t:5c,8c-dimethanonaphthalene-2t,3t,6c,7c-tetracarboxylic2,3:6,7-dianhydride, 2c,3c,6c,7c-tetracarboxylic 2,3:6,7-dianhydride,5-endo-carboxymethylbicyclo[2.2.1]-heptane-2-exo,3-exo,5-exo-tricarboxylicacid 2,3:5,5-dianhydride,5-(2,5-dioxotetrahydro-3-furanyl)-3-methyl-3-cyclohexene-1,2-dicarboxylicanhydride, isomers of bis(aminomethyl)bicyclo[2.2.1]heptane, or4,4′-methylenebis(2-methylcyclohexylamine), pyromellitic dianhydride(PMDA) 3,3′,4,4′-biphenyl dianhydride (4,4′-BPDA),3,3′,4,4′-benzophenone dianhydride (4,4′-BTDA), 3,3′,4,4′-oxydiphthalicanhydride (4,4′-ODPA), 1,4-bis(3,4-dicarboxyl-phenoxy)benzenedianhydride (4,4′-HQDPA), 1,3-bis(2,3-dicarboxyl-phenoxy)benzenedianhydride (3,3′-HQDPA), 4,4′-bis(3,4-dicarboxylphenoxyphenyl)-isopropylidene dianhydride (4,4′-BPADA),4,4′-(2,2,2-trifluoro-1-pentafluorophenylethylidene) diphthalicdianhydride (3FDA), 4,4′-oxydianiline (ODA), m-phenylenediamine (MPD),p-phenylenediamine (PPD), m-toluenediamine (TDA),1,4-bis(4-aminophenoxy)benzene (1,4,4-APB),3,3′-(m-phenylenebis(oxy))dianiline (APB),4,4′-diamino-3,3′-dimethyldiphenylmethane (DMMDA),2,2′-bis(4-(4-aminophenoxy)phenyl)propane (BAPP), 1,4-cyclohexanediamine2,2′-bis[4-(4-aminophenoxy) phenyl] hexafluoroisopropylidene (4-BDAF),6-amino-1-(4′-aminophenyl)-1,3,3-trimethylindane (DAPI), maleicanhydride (MA), citraconic anhydride (CA), nadic anhydride (NA),4-(phenylethynyl)-1,2-benzenedicarboxylic acid anhydride (PEPA),4,4′-diaminobenzanilide (DABA),4,4′-(hexafluoroisopropylidene)di-phthalicanhydride (6-FDA),pyromellitic dianhydride, benzophenone-3,3′,4,4′-tetracarboxylicdianhydride, 3,3′,4,4′-biphenyltetracarboxylic dianhydride,4,4′-(hexafluoroisopropylidene)diphthalic anhydride,perylene-3,4,9,10-tetracarboxylic dianhydride, 4,4′-oxydiphthalicanhydride, 4,4′-(hexafluoroisopropylidene)diphthalic anhydride,4,4′-(4,4′-isopropylidenediphenoxy)bis(phthalic anhydride),1,4,5,8-naphthalenetetracarboxylic dianhydride,2,3,6,7-naphthalenetetracarboxylic dianhydride, as well as thosematerials described in U.S. Pat. Nos. 7,619,042, 8,053,492, 4,880,895,6,232,428, 4,595,548, WO Pub. No. 2007/016516, U.S. Pat. Pub. No.2008/0214777, U.S. Pat. Nos. 6,444,783, 6,277,950, and 4,680,373. FIG.15 depicts the chemical structure of some suitable monomers that may beused to form a polyimide coating applied to the glass body 102. Inanother embodiment, the polyamic acid solution from which the polyimideis formed may comprise poly (pyromelliticdianhydride-co-4,4′-oxydianiline) amic acid (commercially available fromAldrich).

In another embodiment, the polymer chemical composition may comprise afluoropolymer. The fluoropolymer may be a copolymer wherein bothmonomers are highly fluorinated. Some of the monomers of thefluoropolymer may be fluoroethylene. In one embodiment, the polymerchemical composition comprises an amorphous fluoropolymer, such as, butnot limited to, Teflon AF (commercially available from DuPont). Inanother embodiment, the polymer chemical composition comprisesperfluoroalkoxy (PFA) resin particles, such as, but not limited to,Teflon PFA TE-7224 (commercially available from DuPont).

In another embodiment, the polymer chemical composition may comprise asilicone resin. The silicone resin may be a highly branched3-dimensional polymer which is formed by branched, cage-likeoligosiloxanes with the general formula of R_(n)Si(X)_(m)O_(y), where Ris a non reactive substituent, usually methyl or phenyl, and X is OH orH. While not wishing to be bound by theory, it is believed that curingof the resin occurs through a condensation reaction of Si—OH moietieswith a formation of Si—O—Si bonds. The silicone resin may have at leastone of four possible functional siloxane monomeric units, which includeM-resins, D-resins, T-resins, and Q-resins, wherein M-resins refer toresins with the general formula R₃SiO, D-resins refer to resins with thegeneral formula R₂SiO₂, T-resins refer to resins with the generalformula RSiO₃, and Q-resins refer to resins with the general formulaSiO₄ (a fused quartz). In some embodiments resins are made of D and Tunits (DT resins) or from M and Q units (MQ resins). In otherembodiments, other combinations (MDT, MTQ, QDT) are also used.

In one embodiment, the polymer chemical composition comprisesphenylmethyl silicone resins due to their higher thermal stabilitycompared to methyl or phenyl silicone resins. The ratio of phenyl tomethyl moieties in the silicone resins may be varied in the polymerchemical composition. In one embodiment, the ratio of phenyl to methylis about 1.2. In another embodiment, the ratio of phenyl to methyl isabout 0.84. In other embodiments, the ratio of phenyl to methyl moietiesmay be about 0.5, 0.6, 0.7, 0.8, 0.9, 1.0, 1.1, 1.3, 1.4, or 1.5. In oneembodiment, the silicone resin is DC 255 (commercially available fromDow Corning). In another embodiment, the silicone resin is DC806A(commercially available from Dow Corning). In other embodiments, thepolymer chemical composition may comprise any of the DC series resins(commercially available for Dow Corning), and/or Hardsil Series AP andAR resins (commercially available from Gelest). The silicone resins canbe used without coupling agent or with coupling agent.

In another embodiment, the polymer chemical composition may comprisesilsesquioxane-based polymers, such as but not limited to T-214(commercially available from Honeywell), SST-3M01 (commerciallyavailable from Gelest), POSS Imiclear (commercially available fromHybrid Plastics), and FOX-25 (commercially available from Dow Corning).In one embodiment, the polymer chemical composition may comprise asilanol moiety.

Referring again to FIGS. 8 and 12A, the lubricous coating 160 may beapplied in a multi stage process, wherein the glass body 102 iscontacted with the coupling agent solution to form the coupling agentlayer 180 (as described above), and dried, and then contacted with apolymer chemical composition solution, such as a polymer or polymerprecursor solution, such as by a submersion process, or alternatively,the polymer layer 170 may be applied by a spray or other suitable means,and dried, and then cured at high temperatures. Alternatively, if acoupling agent layer 180 is not used, the polymer chemical compositionof the polymer layer 170 may be directly applied to the outer surface106 of the glass body 102. In another embodiment, the polymer chemicalcomposition and the coupling agent may be mixed in the lubricous coating160, and a solution comprising the polymer chemical composition and thecoupling agent may be applied to the glass body 102 in a single coatingstep.

In one embodiment, the polymer chemical composition comprises apolyimide wherein a polyamic acid solution is applied over the couplingagent layer 180. In other embodiments, a polyamic acid derivative may beused, such as, for example, a polyamic acid salt, a polyamic acid ester,or the like. For example, suitable polyamic acid salts may includepolyamic acid salt formed from triethylamine. Other suitable salts mayinclude those salts formed by the deprotonation of the carboxylic acidgroups of the polyamic acids by basic additives leading to an ionicinteraction of the resultant carboxylate group with its conjugate acid.The basic additives may include organic, inorganic, or organometallicspecies or combinations thereof. The inorganic species may includemoieties such as alkalis, alkaline earth, or metal bases. The organicbases (proton acceptors) may include aliphatic amines, aromatic amines,or other organic bases. Aliphatic amines include primary amines such asbut not limited to ethylamine, secondary amines such as but not limitedto diethylamines, and tertiary amines such as triethylamines. Aromaticamines include anilines, pyridines, and imidazoles. Organometallic basescould include 2,2 dimethylpropylmagnesium chlorides or others. In oneembodiment, the polyamic acid solution may comprise a mixture of 1 vol.% polyamic acid and 99 vol % organic solvent. The organic solvent maycomprise a mixture of toluene and at least one of N,N-Dimethylacetamide(DMAc), N,N-Dimethylformamide (DMF), and 1-Methyl-2-pyrrolidinone (NMP)solvents, or a mixture thereof. In one embodiment the organic solventsolution comprises about 85 vol % of at least one of DMAc, DMF, and NMP,and about 15 vol % toluene. However, other suitable organic solvents maybe used. The coated glass container 100 may then be dried at around 150°C. for about 20 minutes, or any time and temperature sufficient toadequately liberate the organic solvent present in the lubricous coating160.

In the layered transient organic lubricous coating embodiment, after theglass body 102 is contacted with the coupling agent to form the couplingagent layer 180 and polyamic acid solution to form the polymer layer170, the coated glass container 100 may be cured at high temperatures.The coated glass container 100 may be cured at 300° C. for about 30minutes or less, or may be cured at a temperature higher than 300° C.,such as at least 320° C., 340° C., 360° C., 380° C., or 400° C. for ashorter time. It is believed, without being bound by theory, that thecuring step imidizes the polyamic acid in the polymer layer 170 byreaction of carboxylic acid moieties and amide moieties to create apolymer layer 170 comprising a polyimide. The curing may also promotebonds between the polyimide and the coupling agent. The coated glasscontainer 100 is then cooled to room temperature.

Furthermore, without being bound by limitation, it is believed that thecuring of the coupling agent, polymer chemical composition, or both,drives off volatile materials, such as water and other organicmolecules. As such, these volatile materials that are liberated duringcuring are not present when the article, if used as a container, isthermally treated (such as for depyrogenation) or contacted by thematerial in which it is a package for, such as a pharmaceutical. Itshould be understood that the curing processes described herein areseparate heating treatments than other heating treatments describedherein, such as those heating treatments similar or identical toprocesses in the pharmaceutical packaging industry, such asdepyrogenation or the heating treatments used to define thermalstability, as described herein.

In one embodiment, the coupling agent comprises a silane chemicalcomposition, such as an alkoxysilane, which may improve the adhesion ofthe polymer chemical composition to the glass body. Without being boundby theory, it is believed that alkoxysilane molecules hydrolyze rapidlyin water forming isolated monomers, cyclic oligomers, and largeintramolecular cyclics. In various embodiments, the control over whichspecies predominates may be determined by silane type, concentration,pH, temperature, storage condition, and time. For example, at lowconcentrations in aqueous solution, aminopropyltrialkoxysilane (APS) maybe stable and form trisilanol monomers and very low molecular weightoligomeric cyclics.

It is believed, still without being bound by theory, that the reactionof one or more silanes chemical compositions to the glass body mayinvolve several steps. As shown in FIG. 17, in some embodiments,following hydrolysis of the silane chemical composition, a reactivesilanol moiety may be formed, which can condense with other silanolmoieties, for example, those on the surface of a substrate, such as aglass body. After the first and second hydrolysable moieties arehydrolyzed, a condensation reaction may be initiated. In someembodiments, the tendency toward self condensation can be controlled byusing fresh solutions, alcoholic solvents, dilution, and by carefulselection of pH ranges. For example, silanetriols are most stable at pH3-6, but condense rapidly at pH 7-9.3, and partial condensation ofsilanol monomers may produce silsesquioxanes. As shown in FIG. 17, thesilanol moieties of the formed species may form hydrogen bonds withsilanol moieties on the substrate, and during drying or curing acovalent bond may be formed with the substrate with elimination ofwater. For example, a moderate cure cycle (110° C. for 15 min) may leavesilanol moieties remaining in free form and, along with any silaneorganofunctionality, may bond with the subsequent topcoat, providingimproved adhesion.

In some embodiments, the one or more silane chemical compositions of thecoupling agent may comprise an amine moiety. Still without being boundby theory, it is believed that this amine moiety may act as a basecatalyst in the hydrolysis and co-condensation polymerization andenhance the adsorption rate of the silanes having an amine moiety on aglass surface. It may also create a high pH (9.0-10.0) in aqueoussolution that conditions the glass surface and increases density ofsurface silanol moieties. Strong interaction with water and proticsolvents maintains solubility and stability of a silane having an aminemoiety chemical composition, such as APS.

In an exemplary embodiment, the glass body 102 may compriseion-exchanged glass and the coupling agent may be a silane. In someembodiments, adhesion of the lubricous coating to an ion-exchanged glassbody may stronger than adhesion of the lubricous coating to anon-ion-exchanged glass body. It is believed, without being bound bytheory, that any of several aspects of ion-exchanged glass may promotebonding and/or adhesion, as compared with non-ion-exchanged glass.First, ion-exchanged glass may have enhanced chemical/hydrolyticstability that may affect stability of the coupling agent and/or itsadhesion to glass surface. Non-ion-exchanged glass typically hasinferior hydrolytic stability and under humid and/or elevatedtemperature conditions, alkali metals could migrate out of the glassbody to the interface of the glass surface and coupling agent layer (ifpresent), or even migrate into the coupling agent layer, if present. Ifalkali metals migrate, as described above, and there is a change in pH,hydrolysis of Si—O—Si bonds at the glass/coupling agent layer interfaceor in the coupling agent layer itself may weaken either the couplingagent mechanical properties or its adhesion to the glass. Second, whenion-exchanged glasses are exposed to strong oxidant baths, such aspotassium nitrite baths, at elevated temperatures, such as 400° C. to450° C., and removed, organic chemical compositions on the surface ofthe glass are removed, making it particularly well suited for silanecoupling agents without further cleaning. For example, anon-ion-exchanged glass may have to be exposed to an additional surfacecleaning treatment, adding time and expense to the process.

In one exemplary embodiment, the coupling agent may comprise at leastone silane comprising an amine moiety and the polymer chemicalcomposition may comprise a polyimide chemical composition. Now referringto FIG. 18, without being bound by theory, it is believed that theinteraction between this amine moiety interaction and the polyamic acidprecursor of the polyimide follows a stepwise process. As shown in FIG.18, the first step is formation of a polyamic acid salt between acarboxyl moiety of the polyamic acid and the amine moiety. The secondstep is thermal conversion of the salt into an amide moiety. The thirdsstep is further conversion of the amide moiety into an imide moiety withscission of the polymer amide bonds. The result is a covalent imideattachment of a shortened polymer chain (polyimide chain) to an aminemoiety of the coupling agent, as shown in FIG. 18.

EXAMPLES

The various embodiments of glass containers with improved attributeswill be further clarified by the following examples. The examples areillustrative in nature, and should not be understood to limit thesubject matter of the present disclosure.

Example 1

Glass vials were formed from Type IB glass having the same compositionas Example 2 of Table 2 above and the glass composition identified as“Example E” of Table 1 of U.S. patent application Ser. No. 13/660,394filed Oct. 25, 2012 and entitled “Glass Compositions with ImprovedChemical and Mechanical Durability” assigned to Corning, Incorporated(hereinafter “the Reference Glass Composition”). The vials were washedwith deionized water, blown dry with nitrogen, and dip coated with a0.1% solution of APS (aminopropylsilsesquioxane). The APS coating wasdried at 100° C. in a convection oven for 15 minutes. The vials werethen dipped into a 0.1% solution of Novastrat® 800 polyamic acid in a15/85 toluene/DMF (dimethylformamide) solution or in a 0.1% to 1%poly(pyromellitic dianhydride-co-4,4′-oxydianiline) amic acid solutionPMDA-ODA (poly(4,4′-oxydiphenylene-pyromellitimide) inN-methyl-2-pyrrolidone (NMP). The coated vials were heated to 150° C.and held for 20 minutes to evaporate the solvents. Thereafter, thecoatings were cured by placing the coated vials into a preheated furnaceat 300° C. for 30 minutes. After curing, the vials coated with the 0.1%solution of Novastrat® 800 had no visible color. However, the vialscoated with the solution of poly(pyromelliticdianhydride-co-4,4′oxydianiline) were visibly yellow in color due to thethickness of the coating. Both coatings exhibited a low coefficient offriction in vial-to-vial contact tests.

Example 2

Glass vials formed from Type IB glass vials formed from the samecomposition as Example 2 of Table 2 above (in as received/uncoated) andvials coated with a lubricous coating were compared to assess the lossof mechanical strength due to abrasion. The coated vials were producedby first ion exchange strengthening glass vials produced from theReference Glass Composition. The ion exchange strengthening wasperformed in a 100% KNO₃ bath at 450° C. for 8 hours. Thereafter, thevials were washed with deionized water, blown dry with nitrogen, and dipcoated with a 0.1% solution of APS (aminopropylsilsesquioxane) in water.The APS coating was dried at 100° C. in a convection oven for 15minutes. The vials were then dipped into a 0.1% solution of Novastrat®800 polyamic acid in a 15/85 toluene/DMF solution. The coated vials wereheated to 150° C. and held for 20 minutes to evaporate the solvents.Thereafter, the coatings were cured by placing the coated vials into apreheated furnace at 300° C. for 30 minutes. The coated vials were thensoaked in 70° C. de-ionized water for 1 hour and heated in air at 320°C. for 2 hours to simulate actual processing conditions.

Unabraded vials formed from the Type IB glass formed from the samecomposition as Example 2 of Table 2 above and unabraded vials formedfrom the ion-exchange strengthened and coated Reference GlassComposition were tested to failure in a horizontal compression test(i.e., a plate was placed over the top of the vial and a plate wasplaced under the bottom of the vial and the plates were pressed togetherand the applied load at failure was determined with a load cell). FIG.19 graphically depicts the failure probability as a function of appliedload in a horizontal compression test for vials formed from a ReferenceGlass Composition, vials formed from a Reference Glass Composition in acoated and abraded condition, vials formed from the Type IB glass, andvials formed from the Type IB glass in an abraded condition. The failureloads of the unabraded vials are graphically depicted in the Weibullplots. Sample vials formed from the Type IB glass and unabraded vialsformed from the ion-exchange strengthened and coated glass were thenplaced in the vial-on-vial jig of FIG. 9 to abrade the vials anddetermine the coefficient of friction between the vials as they wererubbed together. The load on the vials during the test was applied witha UMT machine and was varied between 24 N and 44 N. The applied loadsand the corresponding maximum coefficient of friction are reported inthe Table contained in FIG. 20. For the uncoated vials, the maximumcoefficient of friction varied from 0.54 to 0.71 (shown in FIG. 20 asvial samples “3&4” and “7&8”, respectively) and while for the coatedvials the maximum coefficient of friction varied from 0.19 to 0.41(shown in FIG. 20 as vial samples “15&16” and “12&14”, respectively).Thereafter, the scratched vials were tested in the horizontalcompression test to assess the loss of mechanical strength relative tothe unabraded vials. The failure loads applied to the unabraded vialsare graphically depicted in the Weibull plots of FIG. 19.

As shown in FIG. 19, the uncoated vials had a significant decrease instrength after abrasion whereas the coated vials had a relatively minordecrease in strength after abrasion. Based on these results, it isbelieved that the coefficient of friction between the vials should beless than 0.7 or 0.5, or even less than 0.45 in order to mitigate theloss of strength following vial-on-vial abrasion.

Example 3

In this example, multiple sets of glass tubes were tested in four pointbending to assess their respective strengths. A first set of tubesformed from the Reference Glass Composition was tested in four pointbending in as received condition (uncoated, non-ion exchangestrengthened). A second set of tubes formed from the Reference GlassComposition was tested in four point bending after being ion exchangestrengthened in a 100% KNO₃ bath at 450° C. for 8 hours. A third set oftubes formed from the Reference Glass Composition was tested in fourpoint bending after being ion exchange strengthened in a 100% KNO₃ bathat 450° C. for 8 hours and coated with 0.1% APS/0.1% Novastrat® 800 asdescribed in Example 2. The coated tubes were also soaked in 70° C.de-ionized water for 1 hour and heated in air at 320° C. for 2 hours tosimulate actual processing conditions. These coated tubes were alsoabraded in the vial-on-vial jig shown in FIG. 9 under a 30 N load priorto bend testing. A fourth set of tubes formed from the Reference GlassComposition was tested in four point bending after being ion exchangestrengthened in a 100% KNO₃ bath at 450° C. for 1 hour. These uncoated,ion exchange strengthened tubes were also abraded in the vial-on-vialjig shown in FIG. 9 under a 30 N load prior to bend testing. A fifth setof tubes formed from the Type IB glass was tested in four point bendingin as received condition (uncoated, non-ion exchange strengthened). Asixth set of tubes formed from the Type IB glass was tested in fourpoint bending after being ion exchange strengthened in a 100% KNO₃ bathat 450° C. for 1 hour. The results of testing are graphically depictedin the Weibull plots displayed in FIG. 21.

Referring to FIG. 21, the second set of tubes which were non-abraded andformed from the Reference Glass Composition and ion exchangestrengthened withstood the highest stress before breaking. The third setof tubes which were coated with the 0.1% APS/0.1% Novastrat® 800 priorto abrading showed a slight reduction in strength relative to theiruncoated, non-abraded equivalents (i.e., the second set of tubes).However, the reduction in strength was relatively minor despite beingsubjected to abrading after coating.

Example 4

Two sets of vials were prepared and run through a pharmaceutical fillingline. A pressure sensitive tape (commercially available from Fujifilm)was inserted in between the vials to measure contact/impact forcesbetween the vials and between the vials and the equipment. The first setof vials was formed from Type 1B glass and was not coated. The secondset of vials was formed from the Reference Glass Composition and wascoated with a low-friction polyimide based coating having a coefficientof friction of about 0.25, as described above. The pressure sensitivetapes were analyzed after the vials were run through the pharmaceuticalfilling line and demonstrated that the coated vials of the second setexhibited a 2-3 times reduction in stress compared to the un-coatedvials of the first set.

Example 5

Three sets of four vials each were prepared. All the vials were formedfrom the Reference Glass Composition. The first set of vials was coatedwith the APS/Novastrat® 800 coating as described in Example 2. Thesecond set of vials was dip coated with 0.1% DC806A in toluene. Thesolvent was evaporated at 50° C. and the coating was cured at 300° C.for 30 min. Each set of vials was placed in a tube and heated to 320° C.for 2.5 hours under an air purge to remove trace contaminants adsorbedinto the vials in the lab environment. Each set of samples was thenheated in the tube for another 30 minutes and the outgassed volatileswere captured on an activated carbon sorbent trap. The trap was heatedto 350° C. over 30 minutes to desorb any captured material which was fedinto a gas chromatograph-mass spectrometer. FIG. 22 depicts gaschromatograph-mass spectrometer output data for the APS/Novastrat® 800coating. FIG. 23 depicts gas chromatography-mass spectrometer outputdata for the DC806A coating. No outgassing was detected from the 0.1%APS/0.1% Novastrat® 800 coating or the DC806A coating.

A set of four vials was coated with a tie-layer using 0.5%/0.5%GAPS/APhTMS (3-aminopropyltrimethoxysilane/aminophenyltrimethoxysilane)solution in methanol/water mixture. Each vial had a coated surface areaof about 18.3 cm². Solvent was allowed to evaporate at 120° C. for 15min from the coated vials. Then a 0.5% Novastrat® 800 solution indimethylacetamide was applied onto the samples. The solvent wasevaporated at 150° C. for 20 min. These uncured vials were subjected toan outgassing test described above. The vials were heated to 320° C. ina stream of air (100 mL/min) and upon reaching 320° C. the outgassedvolatiles were captured on an activated carbon sorbent traps every 15min. The traps then were heated to 350° C. over 30 minutes to desorb anycaptured material which was fed into a gas chromatograph-massspectrometer. Table 3 shows the amount of captured materials over thesegments of time that the samples were held at 320° C. Time zerocorresponds with the time that the sample first reached a temperature of320° C. As seen in Table 3, after 30 min of heating the amount ofvolatiles decreases below the instrument detection limit of 100 ng.Table 3 also reports the volatiles lost per square cm of coated surface.

TABLE 3 Volatiles per vial and per coated area. Amount, Amount TimePeriod at 320° C. ng/vial ng/cm² 25° C. to 320° C. ramp (t = 0) 604043301 t = 0 to 15 min 9371 512 t = 15 to 30 min 321 18 t = 30 to 45 min<100 <5 t = 45 to 60 min <100 <5 t = 60 to 90 min <100 <5

Example 6

A plurality of vials was prepared with various coatings based on siliconresin or polyimides with and without coupling agents. When couplingagents were used, the coupling agents included APS and GAPS, which is aprecursor for APS. The outer coating layer was prepared from Novastrat®800, the poly(pyromellitic dianhydride-co-4,4′oxydianiline) describedabove, or silicone resins such as DC806A and DC255. TheAPS/poly(4,4′-oxydiphenylene-pyromellitimide) coatings were preparedusing a 0.1% solution of APS (aminopropylsilsesquioxane) and 0.1%solution, 0.5% solution or 1.0% solutions of poly(pyromelliticdianhydride-co-4,4′-oxydianiline) amic acid PMDA-ODApoly(4,4′-oxydiphenylene-pyromellitimide)) in N-methyl-2-pyrrolidone(NMP). The poly(4,4′-oxydiphenylene-pyromellitimide) coatings were alsoapplied without a coupling agent using a 1.0% solution of thepoly(pyromellitic dianhydride-co-4,4′oxydianiline) in NMP. TheAPS/Novastrat® 800 coatings were prepared using a 0.1% solution of APSand a 0.1% solution of Novastrat® 800 polyamic acid in a 15/85toluene/DMF solution. The DC255 coatings were applied directly to theglass without a coupling agent using a 1.0% solution of DC255 inToluene. The APS/DC806A coatings were prepared by first applying a 0.1%solution of APS in water and then a 0.1% solution or a 0.5% solution ofDC806A in toluene. The GAPS/DC806A coatings were applied using a 1.0%solution of GAPS in 95 wt. % ethanol in water as a coupling agent andthen a 1.0% solution of DC806A in toluene. The coupling agents andcoatings were applied using dip coating methods as described herein withthe coupling agents being heat treated after application and the siliconresin and polyimide coatings being dried and cured after application.The coating thicknesses were estimated based on the concentrations ofthe solutions used. The Table contained in FIG. 24 lists the variouscoating compositions, estimated coating thicknesses and testingconditions.

Thereafter, some of the vials were tumbled to simulate coating damageand others were subjected to abrasion under 30 N and 50 N loads in thevial-on-vial jig depicted in FIG. 9. Thereafter, all the vials weresubjected to a lyophilization (freeze drying process) in which the vialswere filled with 0.5 mL of sodium chloride solution and then frozen at−100° C. Lyophilization was then performed for 20 hours at −15° C. undervacuum. The vials were inspected with optical quality assuranceequipment and under microscope. No damage to the coatings was observeddue to lyophilization.

Example 7

Three sets of six vials were prepared to assess the effect of increasingload on the coefficient of friction for uncoated vials and vials coatedwith Dow Corning DC 255 silicone resin. A first set of vials was formedfrom Type IB glass and left uncoated. The second set of vials was formedfrom the Reference Glass Composition and coated with a 1% solution ofDC255 in Toluene and cured at 300° C. for 30 min. The third set of vialswas formed from the Type IB glass and coated with a 1% solution of DC255in Toluene. The vials of each set were placed in the vial-on-vial jigdepicted in FIG. 9 and the coefficient of friction relative to asimilarly coated vial was measured during abrasion under static loads of10 N, 30 N, and 50 N. The results are graphically reported in FIG. 25.As shown in FIG. 25, coated vials showed appreciably lower coefficientsof friction compared to uncoated vials when abraded under the sameconditions irrespective of the glass composition.

Example 8

Three sets of two glass vials were prepared with anAPS/poly(4,4′-oxydiphenylene-pyromellitimide) coating. First, each ofthe vials was dip coated in a 0.1% solution of APS(aminopropylsilsesquioxane). The APS coating was dried at 100° C. in aconvection oven for 15 minutes. The vials were then dipped into a 0.1%poly(pyromellitic dianhydride-co-4,4′-oxydianiline) amic acid solution(PMDA-ODA (poly(4,4′-oxydiphenylene-pyromellitimide)) inN-methyl-2-pyrrolidone (NMP). Thereafter, the coatings were cured byplacing the coated vials into a preheated furnace at 300° C. for 30minutes.

Two vials were placed in the vial-on-vial jig depicted in FIG. 9 andabraded under a 10 N load. The abrasion procedure was repeated 4 moretimes over the same area and the coefficient of friction was determinedfor each abrasion. The vials were wiped between abrasions and thestarting point of each abrasion was positioned on a previouslynon-abraded area. However, each abrasion traveled over the same “track”.The same procedure was repeated for loads of 30 N and 50 N. Thecoefficients of friction of each abrasion (i.e., A1-A5) are graphicallydepicted in FIG. 26 for each load. As shown in FIG. 26, the coefficientof friction of the APS/poly(4,4′-oxydiphenylene-pyromellitimide) coatedvials was generally less than 0.30 for all abrasions at all loads. Theexamples demonstrate improved resistance to abrasion for polyimidecoating when applied over a glass surface treated with a coupling agent.

Example 9

Three sets of two glass vials were prepared with an APS coating. Each ofthe vials were dip coated in a 0.1% solution of APS(aminopropylsilsesquioxane) and heated at 100° C. in a convection ovenfor 15 minutes. Two vials were placed in the vial-on-vial jig depictedin FIG. 9 and abraded under a 10 N load. The abrasion procedure wasrepeated 4 more times over the same area and the coefficient of frictionwas determined for each abrasion. The vials were wiped between abrasionsand the starting point of each abrasion was positioned on a previouslynon-abraded area. However, each abrasion traveled over the same “track”.The same procedure was repeated for loads of 30 N and 50 N. Thecoefficients of friction of each abrasion (i.e., A1-A5) are graphicallydepicted in FIG. 27 for each load. As shown in FIG. 27, the coefficientof friction of the APS only coated vials is generally higher than 0.3and often reached 0.6 or even higher.

Example 10

Three sets of two glass vials were prepared with anAPS/poly(4,4′-oxydiphenylene-pyromellitimide) coating. Each of the vialswas dip coated in a 0.1% solution of APS (aminopropylsilsesquioxane).The APS coating was heated at 100° C. in a convection oven for 15minutes. The vials were then dipped into a 0.1% poly(pyromelliticdianhydride-co-4,4′-oxydianiline) amic acid solution (PMDA-ODA(poly(4,4′-oxydiphenylene-pyromellitimide)) in N-methyl-2-pyrrolidone(NMP). Thereafter, the coatings were cured by placing the coated vialsinto a preheated furnace at 300° C. for 30 minutes. The coated vialswere then depyrogenated (heated) at 300° C. for 12 hours.

Two vials were placed in the vial-on-vial jig depicted in FIG. 9 andabraded under a 10 N load. The abrasion procedure was repeated 4 moretimes over the same area and the coefficient of friction was determinedfor each abrasion. The vials were wiped between abrasions and thestarting point of each abrasion was positioned on a previously abradedarea and each abrasion was performed over the same “track”. The sameprocedure was repeated for loads of 30 N and 50 N. The coefficients offriction of each abrasion (i.e., A1-A5) are graphically depicted in FIG.28 for each load. As shown in FIG. 28, the coefficients of friction ofthe APS/poly(4,4′-oxydiphenylene-pyromellitimide) coated vials weregenerally uniform and approximately 0.20 or less for the abrasionsintroduced at loads of 10 N and 30 N. However, when the applied load wasincreased to 50 N, the coefficient of friction increased for eachsuccessive abrasion, with the fifth abrasion having a coefficient offriction slightly less than 0.40.

Example 11

Three sets of two glass vials were prepared with an APS(aminopropylsilsesquioxane) coating. Each of the vials was dip coated ina 0.1% solution of APS and heated at 100° C. in a convection oven for 15minutes. The coated vials were then depyrogenated (heated) at 300° C.for 12 hours. Two vials were placed in the vial-on-vial jig depicted inFIG. 9 and abraded under a 10 N loaded. The abrasion procedure wasrepeated 4 more times over the same area and the coefficient of frictionwas determined for each abrasion. The vials were wiped between abrasionsand the starting point of each abrasion was positioned on a previouslyabraded area and each abrasion traveled over the same “track”. The sameprocedure was repeated for loads of 30 N and 50 N. The coefficients offriction of each abrasion (i.e., A1-A5) are graphically depicted in FIG.29 for each load. As shown in FIG. 29, the coefficients of friction ofthe APS coated vials depyrogenated for 12 hours were significantlyhigher than the APS coated vials shown in FIG. 27 and were similar tocoefficients of friction exhibited by uncoated glass vials, indicatingthat the vials may have experienced a significant loss of mechanicalstrength due to the abrasions.

Example 12

Three sets of two glass vials formed from the Type IB glass wereprepared with a poly(4,4′-oxydiphenylene-pyromellitimide) coating. Thevials were dipped into a 0.1% poly(pyromelliticdianhydride-co-4,4′-oxydianiline) amic acid solution (PMDA-ODA(poly(4,4′-oxydiphenylene-pyromellitimide)) in N-Methyl-2-pyrrolidone(NMP). Thereafter, the coatings were dried at 150° C. for 20 min andthen cured by placing the coated vials in into a preheated furnace at300° C. for 30 minutes.

Two vials were placed in the vial-on-vial jig depicted in FIG. 9 andabraded under a 10 N loaded. The abrasion procedure was repeated 4 moretimes over the same area and the coefficient of friction was determinedfor each abrasion. The vials were wiped between abrasions and thestarting point of each abrasion was positioned on a previouslynon-abraded area. However, each abrasion traveled over the same “track”.The same procedure was repeated for loads of 30 N and 50 N. Thecoefficients of friction of each abrasion (i.e., A1-A5) are graphicallydepicted in FIG. 30 for each load. As shown in FIG. 30, the coefficientsof friction of the poly(4,4′-oxydiphenylene-pyromellitimide) coatedvials generally increased after the first abrasion demonstrating poorabrasion resistance of a polyimide coating applied onto a glass withouta coupling agent.

Example 13

The APS/Novastrat® 800 coated vials of Example 6 were tested for theircoefficient of friction after lyophilization using a vial-on-vial jigshown in FIG. 9 with a 30 N load. No increase in coefficient of frictionwas detected after lyophilization. FIG. 31 contains Tables showing thecoefficient of friction for the APS/Novastrat® 800 coated vials beforeand after lyophilization.

Example 14

The Reference Glass Composition vials were ion exchanged and coated asdescribed in Example 2. The coated vials were autoclaved using thefollowing protocol: 10 minute steam purge at 100° C., followed by a 20minute dwelling period wherein the coated glass container 100 is exposedto a 121° C. environment, followed by 30 minutes of treatment at 121° C.The coefficient of friction for autoclaved and non-autoclaved vials wasmeasured using a vial-on-vial jig shown in FIG. 9 with 30 N load. FIG.32 shows the coefficient of friction for APS/Novastrat® 800 coated vialsbefore and after autoclaving. No increase in coefficient of friction wasdetected after autoclaving.

Example 15

Three sets of vials were coated with a APS/APhTMS (1:8 ratio) tie-layerand the outer layer consisting of the Novastrat® 800 polyimide appliedas a solution of polyamic acid in dimethylacetamide and imidized at 300°C. One set was depyrogenated for 12 hours at 320° C. The second set wasdepyrogenated for 12 hours at 320° C. and then autoclaved for 1 hour at121° C. A third set of vials was left uncoated. Each set of vials wasthen subjected to a vial-on-vial test under a 30 N load. The coefficientof friction for each set of vials is reported in FIG. 33. Photographs ofthe vial surface showing damage (or the lack of damage) experienced byeach vial is also depicted in FIG. 33. As shown in FIG. 33, the uncoatedvials generally had a coefficient of friction greater than about 0.7.The uncoated vials also incurred visually perceptible damage as a resultof the testing. However, the coated vials had a coefficient of frictionof less than 0.45 without any visually perceptible surface damage.

The coated vials were also subjected to depyrogenation, as describedabove, autoclave conditions, or both. FIG. 34 graphically depicts thefailure probability as a function of applied load in a horizontalcompression test for the vials. There was no statistical differencebetween depyrogenated vials and depyrogenated and autoclaved vials.

Example 16

Vials formed from Type IB ion-exchanged glass were prepared withlubricous coatings have varying ratios of silanes. Referring now to FIG.35, the vials were prepared with three different coating compositions toassess the effect of different ratios of silanes on the coefficient offriction of the applied coating. The first coating composition includeda coupling agent layer having a 1:1 ratio of GAPS toaminophenyltrimethyloxysilane (APhTMS) and an outer coating layer whichconsisted of 1.0% Novastrat® 800 polyimide. The second coatingcomposition included a coupling agent layer having a 1:0.5 ratio of GAPSto APhTMS and an outer coating layer which consisted of 1.0% Novastrat®800 polyimide. The third coating composition included a coupling agentlayer having a 1:0.2 ratio of GAPS to APhTMS and an outer coating layerwhich consisted of 1.0% Novastrat® 800 polyimide. All the vials weredepyrogenated for 12 hours at 320° C. Thereafter, the vials weresubjected to a vial-on-vial frictive test under loads of 20 N and 30 N.The average applied normal force, coefficient of friction, and maximumfrictive force (Fx) for each vial is reported in FIG. 35. As shown inFIG. 35, decreasing the amount of aromatic silane (i.e., theaminophenytrimethyloxysilane) increases the coefficient of frictionbetween the vials as well as the frictive force experienced by thevials.

Example 17

Vials formed from Type IB ion-exchanged glass were prepared withlubricous coatings have varying ratios of silanes.

Samples were prepared with a composition which included a coupling agentlayer formed from 0.125% APS and 1.0% aminophenyltrimethyloxysilane(APhTMS), having an APS/APhTMS ratio of 1:8, and an outer coating layerformed from 0.1% Novastrat® 800 polyimide. The thermal stability of theapplied coating was evaluated by determining the coefficient of frictionand frictive force of vials before and after depyrogenation.Specifically, coated vials were subjected to a vial-on-vial frictivetest under a load of 30 N. The coefficient of friction and frictiveforce were measured and are plotted in FIG. 36 as a function of time. Asecond set of vials was depyrogenated for 12 hours at 320° C. andsubjected to the same vial-on-vial frictive test under a load of 30 N.The coefficient of friction remained the same both before and afterdepyrogenation indicating that the coatings were thermally stable andprotected the glass surface from frictive damage. A photograph of thecontacted area of the glass is also shown.

Samples were prepared with a composition which included a coupling agentlayer formed from 0.0625% APS and 0.5% APhTMS, having an APS/APhTMSratio of 1:8, and an outer coating layer formed from 0.05% Novastrat®800 polyimide. The thermal stability of the applied coating wasevaluated by determining the coefficient of friction and frictive forceof vials before and after depyrogenation. Specifically, coated vialswere subjected to a vial-on-vial frictive test under a load of 30 N. Thecoefficient of friction and frictive force were measured and are plottedin FIG. 37 as a function of time/distance. A second set of vials weredepyrogenated for 12 hours at 320° C. and subjected to the samevial-on-vial frictive test under a load of 30 N. The coefficient offriction remained the same both before and after depyrogenationindicating that the coatings were thermally stable. A photograph of thecontacted area of the glass is also shown.

FIG. 38 graphically depicts the failure probability as a function ofapplied load in a horizontal compression test for the vials withlubricous coatings formed from 0.125% APS and 1.0% APhTMS, and an outercoating layer formed from 0.1% Novastrat® 800 polyimide (Shown as “260”on FIG. 38), and formed from 0.0625% APS and 0.5% APhTMS and an outercoating layer formed from 0.05% Novastrat® 800 polyimide (Shown as “280”on FIG. 38). The data shows that failure load remains unchanged fromuncoated unscratched samples for coated, depyrogenated, and scratchedsamples demonstrating glass protection from damage by the coating.

Vials were prepared with lubricous coatings using GAPS hydrolysate.Samples were prepared with a composition which included a coupling agentlayer formed from 0.5% Dynasylan® Hydrosil 1151 (3-aminopropylsilanehydrolysate) and 0.5% aminophenyltrimethyloxysilane (APhTMS), having aratio of 1:1, and an outer coating layer formed from 0.05% Novastrat®800 polyimide. The coating performance was evaluated by determining thecoefficient of friction and frictive force of vials before and afterdepyrogenation. Specifically, Type 1B vials that were ion exchangestrengthened (100% KNO₃ at 450° C., 8 h) were subjected to avial-on-vial frictive test under a load of 30 N. The coefficient offriction and frictive force were measured and are plotted in FIG. 39 asa function of time/distance. A second set of vials were depyrogenatedfor 12 hours at 320° C. and subjected to the same vial-on-vial frictivetest under a load of 30 N. The coefficient of friction remained the sameboth before and after depyrogenation indicating that the coatings werethermally stable. A photograph of the contacted area of the glass isalso shown. This suggests that hydrolysates of aminosilanes are usefulin the coating formulations as well.

The thermal stability of the applied coating was also evaluated for aseries of depyrogenation conditions. Specifically, Type IB ion-exchangedglass vials were prepared with a composition which included a couplingagent layer having a 1:1 ratio of GAPS (0.5%) toaminophenyltrimethyloxysilane (APhTMS) (0.5%) and an outer coating layerwhich consisted of 0.5% Novastrat® 800 polyimide. The vials were dipcoated in the solution using an automated dip coater with a pull-outrate of 2 mm/s. Sample vials were subjected to one of the followingdepyrogenation cycles: 12 hours at 320° C.; 24 hours at 320° C.; 12hours at 360° C.; or 24 hours at 360° C. The coefficient of friction andfrictive force were then measured using a vial-on-vial frictive test andplotted as a function of time for each depyrogenation condition, asshown in FIG. 40. As shown in FIG. 40, the coefficient of friction ofthe vials did not vary with the depyrogenation conditions indicatingthat the coating was thermally stable. FIG. 41 graphically depicts thecoefficient of friction after varying heat treatment times at 360° C.and 320° C.

Example 18

Vials were coated as described in Example 2 with an APS/Novastrat® 800coating. The light transmission of coated vials, as well as uncoatedvials, was measured within a range of wavelengths between 400-700 nmusing a spectrophotometer. The measurements are performed such that alight beam is directed normal to the container wall such that the beampasses through the lubricous coating twice, first when entering thecontainer and then when exiting it. FIG. 11 graphically depicts thelight transmittance data for coated and uncoated vials measured in thevisible light spectrum from 400-700 nm. Line 440 shows an uncoated glasscontainer and line 442 shows a coated glass container.

Example 19

Vials were coated with a 0.25% GAPS/0.25% APhTMS coupling agent and 1.0%Novastrat® 800 polyimide and were tested for light transmission beforeand after depyrogenation at 320° C. for 12 hours. An uncoated vial wasalso tested. Results are shown in FIG. 42.

Example 20

To improve polyimide coating uniformity, the Novastrat® 800 polyamicacid was converted into polyamic acid salt and dissolved in methanol,significantly faster evaporating solvent compared to dimethylacetamide,by adding 4 g of triethylamine to 1L of methanol and then addingNovastrat® 800 polyamic acid to form 0.1% solution. Methanol solublesalt of poly(pyromellitic dianhydride-co-4,4′-oxydianiline) amic acidcould be produced.

Coating on Type IB ion-exchanged vials formed from 1.0% GAPS/1.0% APhTMSin methanol/water mixture and 0.1% Novastrat® 800 polyamic acid salt inmethanol. The coated vials were depyrogenated for 12 h at 360° C. andas-coated and depyrogenated samples were abraded in vial-on-vial jig at10 N, 20 N, and 30 N normal loads. No glass damage was observed atnormal forces of 10 N, 20 N, and 30 N. FIG. 43 shows the coefficient offriction, applied force and frictive force for the samples after a heattreatment at 360° C. for 12 hours. FIG. 44 graphically depicts thefailure probability as a function of applied load in a horizontalcompression test for the samples. Statistically the sample series at 10N, 20 N, and 30 N were indistinguishable from each other. The low loadfailure samples broke from origins located away from the scratch.

Thickness of the coating layers was estimated using ellipsometry andscanning electron microscopy (SEM) is, shown in FIGS. 45-47,respectively. The samples for coating thickness measurements wereproduced using silicon wafer (ellipsometry) and glass slides (SEM). Themethods show thicknesses varying from 55 to 180 nm for the tie-layer and35 nm for Novastrat® 800 polyamic acid salt.

Example 21

Plasma cleaned Si wafer pieces were dip coated using 0.5% GAPS/0.5%APhTMS solution in 75/25 methanol/water vol/vol mixture. The coating wasexposed to 120° C. for 15 minutes. The coating thickness was determinedusing ellipsometry. Three samples were prepared, and had thicknesses of92.1 nm, 151.7 nm, and 110.2 nm, respectively, with a standard deviationof 30.6 nm.

Glass slides were dip coated and examined with a scanning electronmicroscope. FIG. 45 shows an SEM image of a glass slide dip coated in acoating solution of 1.0% GAPS, 1.0% APhTMS, and 0.3% NMP in 75/25methanol/water mixture with an 8 mm/s pull-out followed by curing at150° C. for 15 minutes. The coating appears to be about 93 nm thick.FIG. 46 shows an SEM image of a glass slide dip coated in a coatingsolution of 1.0% GAPS, 1.0% APhTMS, and 0.3 NMP in a 75/25methanol/water mixture with a 4 mm/s pull-out rate followed by curing at150° C. for 15 minutes. The coating appears to be about 55 nm thick.FIG. 47 shows an SEM image of a glass slide dip coated in a coatingsolution of 0.5% Novastrat® 800 solution with a 2 mm/s pull-out ratefollowed by curing at 150° C. for 15 min and heat treatment at 320° C.for 30 minutes. The coating appears to be about 35 nm thick.

Comparative Example A

Glass vials formed from a Type IB glass were coated with a dilutedcoating of Bayer Silicone aqueous emulsion of Baysilone M with a solidscontent of about 1-2%. The vials were treated at 150° C. for 2 hours todrive away water from the surface leaving a polydimethylsiloxane coatingon the exterior surface of the glass. The nominal thickness of thecoating was about 200 nm. A first set of vials were maintained inuntreated condition (i.e., the “as-coated vials”). A second set of vialswere treated at 280° C. for 30 minutes (i.e., the “treated vials”). Someof the vials from each set were first mechanically tested by applying ascratch with a linearly increasing load from 0-48N and a length ofapproximately 20 mm using a UMT-2 tribometer and a vial-on-vial testjig. The scratches were evaluated for coefficient of friction andmorphology to determine if the scratching procedure damaged the glass orif the coating protected the glass from damage due to scratching.

FIG. 48 is a plot showing the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for theas-coated vials. As graphically depicted in FIG. 48, the as-coated vialsexhibited a coefficient of friction of approximately 0.03 up to loads ofabout 30 N. The data shows that below approximately 30 N the COF isalways below 0.1. However, at normal forces greater than 30 N, thecoating began to fail, as indicated by the presence of glass checkingalong the length of scratch. Glass checking is indicative of glasssurface damage and an increased propensity of the glass to fail as aresult of the damage.

FIG. 49 is a plot showing the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for thetreated vials. For the treated vials, the coefficient of frictionremained low until the applied load reached a value of approximately 5N. At that point the coating began to fail and the glass surface wasseverely damaged as evident from the increased amount of glass checkingwhich occurred with increasing load. The coefficient of friction of thetreated vials increased to about 0.5. However, the coating failed toprotect the surface of the glass at loads of 30 N following thermalexposure, indicating that the coating was not thermally stable.

The vials were then tested by applying 30 N static loads across theentire length of the 20 mm scratch. Ten samples of as-coated vials andten samples of treated vials were tested in horizontal compression byapplying a 30 N static load across the entire length of the 20 mmscratch. None of the as-coated samples failed at the scratch while 6 ofthe 10 treated vials failed at the scratch indicating that the treatedvials had lower retained strength.

Comparative Example B

A solution of Wacker Silres MP50 (part #60078465 lot #EB21192) wasdiluted to 2% and was applied to vials formed from the Reference GlassComposition. The vials were first cleaned by applying plasma for 10seconds prior to coating. The vials were dried at 315° C. for 15 minutesto drive off water from the coating. A first set of vials was maintainedin “as-coated” condition. A second set of vials was treated for 30minutes at temperatures ranging from 250° C. to 320° C. (i.e., “treatedvials”). Some of the vials from each set were first mechanically testedby applying a scratch with a linearly increasing load from 0-48N and alength of approximately 20 mm using a UMT-2 tribometer. The scratcheswere evaluated for coefficient of friction and morphology to determineif the scratching procedure damaged the glass or if the coatingprotected the glass from damage due to scratching.

FIG. 50 is a plot showing the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for theas-coated vials.

FIG. 51 is a plot showing the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for thetreated vials treated at 280° C. The treated vials exhibited significantglass surface damage at applied loads greater than about 20N. It wasalso determined that the load threshold to glass damage decreased withincreasing thermal exposure temperatures, indicating that the coatingsdegraded with increasing temperature (i.e., the coating is not thermallystable). Samples treated at temperatures lower than 280° C. showed glassdamage at loads above 30N.

Comparative Example C

Vials formed from the Reference Glass Composition were treated withEvonik Silikophen P 40/W diluted to 2% solids in water. The samples werethen dried at 150° C. for 15 minutes and subsequently cured at 315° C.for 15 minutes. A first set of vials was maintained in “as-coated”condition. A second set of vials was treated for 30 minutes at atemperature of 260° C. (i.e., “the 260° C. treated vials”). A third setof vials was treated for 30 minutes at a temperature of 280° C. (i.e.,“the 280° C. treated vials”). The vials were scratched with a staticload of 30 N using the testing jig depicted in FIG. 9. The vials werethen tested in horizontal compression. The 260° C. treated vials and the280° C. treated vials failed in compression while 2 of 16 of theas-coated vials failed at the scratch. This indicates that the coatingdegraded upon exposure to elevated temperatures and, as a result, thecoating did not adequately protect the surface from the 30 N load.

Example 22

Vials formed from the Reference Glass Composition were coated with asolution of 1.0%/1.0% GAPS/m-APhTMS solution in methanol/water with a75/25 concentration. The vials were dip coated in the solution with apull-out rate of 2 mm/s. The coating was cured at 150° C. for 15minutes. A first set of vials was maintained in untreated condition(i.e., the “as-coated vials”). A second set of vials was depyrogenatedat 300° C. for 12 hours (i.e., the “treated vials”). Some of the vialsfrom each set were mechanically tested by applying a scratch with a 10Nload from the shoulder of the vial to the heel of the vial using a UMT-2tribometer and a vial-on-vial test jig. Additional vials from each setwere mechanically tested by applying a scratch with a 30N load from theshoulder of the vial to the heel of the vial using a UMT-2 tribometerand a vial-on-vial test jig. The scratches were evaluated forcoefficient of friction and morphology to determine if the scratchingprocedure damaged the glass or if the coating protected the glass fromdamage due to scratching.

FIGS. 52 and 53 are plots showing the coefficient of friction, scratchpenetration, applied normal force, and frictional force (y-ordinates) asa function of the length of the applied scratch (x-ordinate) for theas-coated vials. As graphically depicted in FIGS. 52 and 53, the as theas-coated vials exhibited some scuffing and glass damage followingtesting. However, the coefficient of friction was approximately 0.4-0.5during testing. FIGS. 54 and 55 depict the results of similar testingperformed on the treated vials. Following testing, the treated vialsexhibited some abrasion of the surface of the coating as well as somedamage to the glass. The coefficient of friction was approximately0.7-0.8 during testing.

Example 23

Vials formed from the Reference Glass Composition were coated with asolution of 1.0%/1.0% GAPS/m-APhTMS solution in methanol/water with a75/25 concentration. The vials were dip coated in the solution andpulled out at pull-out rates ranging from 0.5 mm/s to 4 mm/s to vary thethickness of the coating on respective vials. The coating was cured at150° C. for 15 minutes. A first set of vials were maintained inuntreated condition (i.e., the “as-coated vials”). A second set of vialswere depyrogenated at 300° C. for 12 hours (i.e., the “treated vials”).Some of the vials from each set were mechanically tested by applying ascratch with a 10N load from the shoulder of the vial to the heel of thevial using a UMT-2 tribometer. Additional vials from each set weremechanically tested by applying a scratch with a 30N load from theshoulder of the vial to the heel of the vial using a UMT-2 tribometer.The vials were then tested in horizontal compression. The results of thehorizontal compression tests are reported in FIGS. 56 and 57. The vialsscratched under a 10N load showed only minimal difference in mechanicalstrength despite the variation in coating thickness. The vials scratchedunder a 30N and having a thinner coating (i.e., a coating correspondingto a 0.5 mm/s pull-out rate) exhibited a greater propensity for failurein horizontal compression relative to vials having a relatively thickercoating.

It should now be understood that the glass containers described hereinhave at least two performance attributes selected from resistance todelamination, improved strength, and increased damage resistance. Forexample, the glass containers may have a combination of resistance todelamination and improved strength; improved strength and increaseddamage resistance; or resistance to delamination and increased damageresistance. These glass containers may be understood in terms of variousaspects.

In a first aspect, a glass container may include a body having an innersurface, an outer surface and a wall thickness extending between theouter surface and the inner surface. A compressively stressed layer mayextend from the outer surface of the body into the wall thickness. Thecompressively stressed layer may have a surface compressive stressgreater than or equal to 150 MPa. A lubricous coating may be positionedaround at least a portion of the outer surface of the body. The outersurface of the body with the lubricous coating may have a coefficient offriction less than or equal to 0.7.

In a second aspect, a glass container may include a body having an innersurface, an outer surface and a wall thickness extending between theouter surface and the inner surface. The body may be formed from a Type1, Class B glass according to ASTM Standard E438-92. A compressivelystressed layer may extend from the outer surface of the body into thewall thickness. The compressively stressed layer may have a surfacecompressive stress greater than or equal to 150 MPa. A lubricous coatingmay be positioned around at least a portion of the outer surface of thebody. The outer surface of the body with the lubricous coating may havea coefficient of friction less than or equal to 0.7.

A third aspect includes the glass container of the first through secondaspects, wherein the surface compressive stress is greater than or equalto 200 MPa.

A fourth aspect includes the glass container of any of the first throughthird aspects, wherein the surface compressive stress is greater than orequal to 300 MPa.

A fifth aspect includes the glass container of any of the first throughfourth aspects, wherein the compressively stressed layer extends to adepth of layer greater than or equal to 3 μm.

A sixth aspect includes the glass container of any of the first throughfifth aspects, wherein the compressively stressed layer extends to adepth of layer greater than or equal to 25 μm.

A seventh aspect includes the glass container of any of the firstthrough sixth aspects, wherein the body is ion-exchange strengthened.

An eighth aspect includes the glass container of any of the firstthrough seventh aspects, wherein the body is high-temperatureion-exchange strengthened.

A ninth aspect includes the glass container of any of the first throughsixth aspects, wherein the body is thermally tempered.

A tenth aspect includes the glass container of the ninth aspect, whereinthe compressively stressed layer extends into the wall thickness to adepth of layer of up to about 22% of the wall thickness.

An eleventh aspect includes the glass container of any of the firstthrough sixth aspects, wherein the body comprises laminated glass.

A twelfth aspect includes the glass container of the eleventh aspect,wherein the laminated glass comprises: a core layer having a corecoefficient of thermal expansion CTE_(core); and at least one claddinglayer fused to the core layer and having a second coefficient of thermalexpansion CTE_(clad), wherein CTE_(core) is not equal to CTE_(clad).

A thirteenth aspect includes the glass container of the twelfth aspect,wherein: the at least one cladding layer comprises a first claddinglayer and a second cladding layer; the first cladding layer is fused toa first surface of the core layer and the second cladding layer is fusedto a second surface of the core layer; and CTE_(core) is greater thanCTE_(clad).

A fourteenth aspect includes the glass container of any of the twelfththrough thirteenth aspects, wherein the compressively stressed layerextends into the wall thickness to a depth of layer which is from about1 μm to about 90% of the wall thickness.

A fifteenth aspect includes the glass container of any of the twelfththrough thirteenth aspects, wherein the compressively stressed layerextends into the wall thickness to a depth of layer which is from about1 μm to about 33% of the wall thickness.

A sixteenth aspect includes the glass container of any of the twelfththrough fifteenth aspects, wherein the at least one cladding layer formsthe inner surface of the body.

A seventeenth aspect includes the glass container of any of the firstthrough sixteenth aspects further comprising an inorganic coatingpositioned on at least a portion of the outer surface of the glass body,wherein the inorganic coating has a coefficient of thermal expansionwhich is less than a coefficient of thermal expansion of the glass body.

An eighteenth aspect includes the glass container of any of the firstthrough seventeenth aspects, wherein the lubricous coating is thermallystable at a temperature of at least about 250° C. for 30 minutes.

A nineteenth aspect includes the glass container of any of the firstthrough eighteenth aspects, wherein the lubricous coating is thermallystable at a temperature of at least about 260° C. for 30 minutes.

A twentieth aspect includes the glass container of any of the firstthrough nineteenth aspects, wherein the lubricous is thermally stable ata temperature of at least about 280° C. for 30 minutes.

A twenty-first aspect includes the glass container of any of the firstthrough twentieth aspects, wherein the lubricous coating is a tenaciousinorganic coating.

A twenty-second aspect includes the glass container of the twenty-firstaspect, wherein the tenacious inorganic coating is a metal nitridecoating, a metal oxide coating, a metal sulfide coating, SiO₂,diamond-like carbide, graphenes or a carbide coating.

A twenty-third aspect includes the glass container of the twenty-firstaspect, wherein the tenacious inorganic coating comprises at least oneof TiN, BN, HBN, TiO₂, Ta₂O₅, HfO₂, Nb₂O₅, V₂O₅, SiO₂, MoS₂, SiC, SnO,SnO₂, ZrO₂, Al₂O₃, BN, ZnO, and BC.

A twenty-fourth aspect includes the glass container of any of the firstthrough twentieth aspects, wherein the lubricous coating comprises atenacious organic coating that has a mass loss of less than about 5% ofits mass when heated from a temperature of 150° C. to 350° C. at a ramprate of about 10° C./minute.

A twenty-fifth aspect includes the glass container of the twenty-fourthaspect, wherein the tenacious organic coating comprises a polymerchemical composition.

A twenty-sixth aspect includes the glass container of the twenty-fifthaspect, wherein tenacious organic coating further comprises a couplingagent.

A twenty-seventh aspect includes the glass container of any of the firstthrough seventeenth aspects, wherein the lubricous coating is atransient coating.

A twenty-eighth aspect includes the glass container of thetwenty-seventh aspect, wherein the transient coating pyrolizes attemperatures less than or equal to 300° C. in less than or equal to 1hour.

A twenty-ninth aspect includes the glass container of any of thetwenty-seventh and the twenty-eighth aspects, wherein the transientcoating comprises a mixture of polyoxyethylene glycol, methacrylateresin, melamine formaldehyde resin, and polyvinyl alcohol.

A thirtieth aspect includes the glass container of any of thetwenty-seventh and the twenty-ninth aspects, wherein the transientcoating comprises one or more polysaccharides.

A thirty-first aspect includes the glass container of any of thetwenty-seventh through thirtieth aspects, wherein the transient coatingcomprises polyacrylic acid or a derivative of polyacrylic acid.

A thirty-second aspect includes the glass container of any of thetwenty-seventh through thirty-first aspects, wherein the transientcoating comprises an inorganic salt.

A thirty-third aspect includes the glass container of any of thetwenty-seventh through thirty-second aspects, wherein the transientcoating comprises at least one of: poly(ethylene oxides), poly(propylene oxides), ethylene oxide-propylene oxide copolymers,polyvinyl-pyrrolidinones, polyethyleneimines, poly(methyl vinyl ethers),polyacrylamides, polymethacrylamides, polyurethanes,poly(vinylacetates), polyvinyl formal, polyformaldehydes includingpolyacetals and acetal copolymers, poly(alkyl methacrylates), methylcelluloses, ethyl celluloses, hydroxyethyl celluloses, hydroxypropylcelluloses, sodium carboxymethyl celluloses, methyl hydroxypropylcelluloses, poly (acrylic acids) and salts thereof, poly(methacrylicacids) and salts thereof, ethylene-maleic anhydride copolymers,ethylene-vinyl alcohol copolymers, ethylene-acrylic acid copolymers,vinyl acetate-vinyl alcohol copolymers, methyl vinyl ether-maleicanhydride copolymers, emulsifiable polyurethanes, polyoxyethylenestearates, and polyolefins including polyethylenes, polypropylenes andcopolymers thereof, starches and modified starches, hydrocolloids,polyacryloamide, vegetable and animal fats, wax, tallow, soap,stearine-paraffin emulsions, polysiloxanes of dimethyl or diphenyl ormethyl/phenyl mixtures, perfluorinated siloxanes and other substitutedsiloxanes, alkylsilanes, aromatic silanes, and oxidized polyethylene.

A thirty-fourth aspect includes the glass container of any of the firstthrough thirty-third aspects, wherein a light transmission through theglass container with the lubricous coating is greater than or equal toabout 55% of a light transmission through an uncoated glass containerfor wavelengths of light from about 400 nm to about 700 nm.

It will be apparent to those skilled in the art that variousmodifications and variations can be made to the embodiments describedherein without departing from the spirit and scope of the claimedsubject matter. Thus it is intended that the specification cover themodifications and variations of the various embodiments described hereinprovided such modification and variations come within the scope of theappended claims and their equivalents.

What is claimed is:
 1. A coated glass pharmaceutical package comprising:a glass container having an interior surface and an exterior surface anda wall extending therebetween, wherein the glass container is formedfrom one of a borosilicate glass composition that meets Type 1 criteriaaccording to USP <660> or an alkali aluminosilicate glass having a ClassHGA 1 hydrolytic resistance when tested according to the ISO 720-1985testing standard; and a lubricous coating having a thickness of ≤100microns positioned on at least a portion of the exterior surface,wherein: the portion of the exterior surface of the coated glasspharmaceutical package with the lubricous coating has a coefficient offriction that is at least 20% less than an uncoated glass pharmaceuticalpackage and the coefficient of friction does not increase by more than30% after undergoing a depyrogenation cycle; and a horizontalcompression strength of the portion of the exterior surface of thecoated glass pharmaceutical package with the lubricous coating is atleast 10% greater than an uncoated glass pharmaceutical package and thehorizontal compression strength is not reduced by more than 20% afterundergoing the depyrogenation cycle.
 2. The coated glass pharmaceuticalpackage of claim 1, wherein the lubricous coating is thermally stable ata temperature of at least about 280° C. for 30 minutes.
 3. The coatedglass pharmaceutical package of claim 1, wherein at least the interiorsurface of the glass container has a delamination factor less than orequal to
 10. 4. The coated glass pharmaceutical package of claim 1,wherein the lubricous coating is an inorganic coating comprising atleast one of a metal nitride coating, a metal oxide coating, a metalsulfide coating, SiO₂, diamond-like carbon graphenes, or a carbidecoating.
 5. The coated glass pharmaceutical package of claim 4, whereinthe inorganic coating comprises at least one of TiN, BN, hBN, TiO₂,Ta₂O₅, HfO₂, Nb₂O₅, V₂O₅, SiO₂, MoS₂, SiC, SnO, SnO₂, ZrO₂, Al₂O₃, ZnO,or BC.
 6. The coated glass pharmaceutical package of claim 1, whereinthe coefficient of friction of the coated glass pharmaceutical packageis ≤0.7.
 7. The coated glass pharmaceutical package of claim 1, whereinthe coefficient of friction of the coated glass pharmaceutical packageis ≤0.6.
 8. The coated glass pharmaceutical package of claim 1, whereinthe coefficient of friction of the coated glass pharmaceutical packageis ≤0.5.
 9. The coated glass pharmaceutical package of claim 1, whereinthe coefficient of friction of the coated glass pharmaceutical packageis ≤0.4.
 10. The coated glass pharmaceutical package of claim 1, whereinthe coefficient of friction of the coated glass pharmaceutical packageis ≤0.3.
 11. The coated glass pharmaceutical package of claim 1, whereinthe depyrogenation cycle comprises heating the coated glasspharmaceutical package to a temperature of at least 250° C. for at least30 minutes.
 12. The coated glass pharmaceutical package of claim 1,wherein a light transmission through the coated glass pharmaceuticalpackage is greater than or equal to about 55% of a light transmissionthrough an uncoated glass pharmaceutical package for each wavelengthfrom about 400 nm to about 700 nm after undergoing the depyrogenationcycle.
 13. The coated glass pharmaceutical package of claim 1, whereinthe lubricous coating comprises a polymer.
 14. The coated glasspharmaceutical package of claim 13, wherein the lubricous coatingfurther comprises a coupling agent.
 15. The coated glass pharmaceuticalpackage of claim 14, wherein the coupling agent is in direct contactwith the exterior surface of the glass container and the polymer is indirect contact with the coupling agent.
 16. The coated glasspharmaceutical package of claim 1, wherein the depyrogenation cyclecomprises heating the coated glass pharmaceutical package to atemperature of at least 260° C. for at least 30 minutes.
 17. The coatedglass pharmaceutical package of claim 1, wherein the depyrogenationcycle comprises heating the coated glass pharmaceutical package to atemperature of from about 250° C. to about 400° C. for a time period ofat least 30 minutes.
 18. The coated glass pharmaceutical package ofclaim 1, wherein a light transmission through the portion of theexterior surface of the coated glass pharmaceutical package with thelubricous coating is greater than or equal to about 55% of a lighttransmission through an uncoated glass pharmaceutical package for eachwavelength from about 400 nm to about 700 nm after the depyrogenationcycle.
 19. The coated glass pharmaceutical package of claim 18, whereinthe depyrogenation cycle comprises heating the coated glasspharmaceutical package in air at a temperature of at least about 250° C.for 30 minutes and the coated glass pharmaceutical package is thermallystable after the depyrogenation cycle.
 20. The coated glasspharmaceutical package of claim 17, wherein the glass container has atleast a class S3 acid resistance or better according to DIN 12116.